CN104195493A - A (TiC+CaF2)/gamma-Ni composite material coating and a plasma transferred arc deposition preparing method thereof - Google Patents
A (TiC+CaF2)/gamma-Ni composite material coating and a plasma transferred arc deposition preparing method thereof Download PDFInfo
- Publication number
- CN104195493A CN104195493A CN201410196052.0A CN201410196052A CN104195493A CN 104195493 A CN104195493 A CN 104195493A CN 201410196052 A CN201410196052 A CN 201410196052A CN 104195493 A CN104195493 A CN 104195493A
- Authority
- CN
- China
- Prior art keywords
- coating
- caf
- powder
- tic
- plasma arc
- 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.)
- Pending
Links
Abstract
The invention discloses a (TiC+CaF2)/gamma-Ni in-situ self-generating wear-resistant self-lubricating composite material coating and a plasma transferred arc deposition preparing method thereof. The coating comprises following chemical components: 42.5-46.25 wt% of Ti, 10.63-11.56 wt% of C, 31.88-34.69 wt% of Ni and 7.5-15 wt% of CaF2. The coating adopts TiC as a wear-resistant reinforcing phase, adopts the CaF2 as a solid lubricating phase, adopts gamma-Ni as a base phase, and is synthesized in situ by utilization of a plasma transferred arc deposition technology. The coating is characterized by compact coating structure, fine crystal grains, good metallurgical bonding with substrates, and excellent wear resistance and antifriction performance. The coating and the plasma transferred arc deposition preparation technology thereof can be widely applied for surface wear-resistant antifriction reinforcing processing for molds of nonferrous metal cold deformation processing devices and have a good application prospect.
Description
Technical field
The invention belongs to material technology field, be specifically related to a kind of (TiC+CaF
2)/γ-Ni in-situ authigenic abrasion-proof self-lubricating composite material coating and the deposited preparation method of transferred plasma arc thereof.
Background technology
According to the medium-term and long-term railway network planning of State Council approved, the year two thousand twenty China railways net revenue kilometres will reach more than 120,000 kilometers, and electrization rate is more than 60%.Copper alloy contact wire is the parts of most critical in electrified high-speed railway contact system, not only requires to have high strength, high conductivity, and effects on surface dimensional precision, form accuracy and surface smoothness have high requirement simultaneously.China's electrified high-speed railway early stage of development, electrified high-speed railway relies on import with osculatory always.In recent years, osculatory production technique " is above drawn to connect and is squeezed " in China's independent development, the copper alloy contact wire oxygen level that adopts this explained hereafter to go out is low, uniform crystal particles is tiny, electricity and mechanical property excellent, therefore this technique is adopted by contact net lines manufacturer both at home and abroad gradually, and has changed thus the situation of China's high-speed electric railway with the long-term dependence on import of osculatory.Continuous extruder, cold-rolling mill, huge machine drawing are as the main production equipments in " above draw to connect and squeeze " technique, its most crucial parts are moulds, the surface smoothness of mould and dimensional precision have determined inherence and the visual appearance of osculatory, the wearing no resistance of mould, the short osculatory manufacturing enterprise of always perplexing of problem that work-ing life is relatively short, other non-ferrous metal cold deformation processing industry also exists same problem.
On osculatory production line, contact wire blank bar is in the mould of continuous extruder in continuous extrusion deformation process, contact wire blank bar and dies cavity produce violent friction, temperature is warmed up to rapidly more than 700 ℃ at short notice, the recrystallization temperature that has surpassed Cu, cavity body of mould internal pressure reaches 1000MPa left and right, the Service Environment of high temperature, high pressure, easily cause die surface wearing and tearing, then have influence on dimensional precision and the surface smoothness of contact wire blank bar.In order to reduce the friction between contact wire blank bar and extrusion mould as far as possible, the friction pair that requires contact wire blank bar and extrusion mould to form has lower frictional coefficient, and moulding stock must have good normal temperature and high temperature abrasion resistance; If exploitation has the alloy material integral manufacturing extrusion mould of low-friction coefficient and high-wearing feature, die manufacturing cost will increase greatly; Because the wearing and tearing of material all originate in material surface gradually to internal extended, therefore, adopt advanced Surface Engineering means, at die surface, prepare that frictional coefficient is low, normal temperature and the good advanced coated material of high temperature abrasion resistance, for solving on osculatory production line main cold deformation processing units as the mould premature wear Problem of Failure of continuous extruder, cold-rolling mill and huge machine drawing, from economic angle, consider to there is undoubtedly higher feasibility.
Conventional Surface Engineering means are widely used in the wear-resisting intensive treatment of die surface as technology such as surface chemistry thermal treatment, thermospray, laser claddings.Modified layer thickness, hardness and wear resistance prepared by surface cementation, nitriding and carbo-nitridization technique all can not adapt to the bad working environments of the high contact stress of mould, strong wearing and tearing; The hot spray coating that the mechanical bond of take is main combination, due to coating and base material bonding strength relatively low, also cannot meet service requirements; Laser cladding technology is widely used in the synthetic preparation of high-performance coating, but because equipment manufacturing cost is high, effciency of energy transfer is low, use cost is high, is therefore difficult in a short time large-scale promotion application in civilian industry.The deposited technology of transferred plasma arc has the advantages such as beam energy density is high, equipment manufacturing cost is low, effciency of energy transfer is high, easy and simple to handle, and in recent years, the relevant deposited research of preparing high-performance coating material of transferred plasma arc has obtained increasing concern.The present invention Ti powder, C powder, Ni powder and CaF in varing proportions
2the mixed powder of powder is starting material, utilizes the deposited equipment of DRF-1 type transferred plasma arc of independent research, manufacture cold extrusion die with material Cr12MoV steel surface prepared take come into being TiC sintering metal mutually as wear-resisting wild phase, with the fine platy CaF of disperse distribution
2for solid lubrication phase, the Ni-based sosoloid of supersaturation of a large amount of Ti, the C in-situ authigenic abrasion-proof self-lubricating composite material coating that is matrix of having take solid solution.Coating structure is fine and close, have non-equilibrium rapid solidification features, and pore-free, flawless are good metallurgical binding with base material, have excellent normal temperature and high temperature abrasion resistance and good antifriction performance.This in situ composites coating and the deposited technology of preparing of transferred plasma arc thereof have a good application prospect in the wear-resisting strengthening of die surface field.
Summary of the invention
One of object of the present invention is that a kind of (TiC+CaF is provided
2)/γ-Ni in-situ authigenic abrasion-proof self-lubricating composite material coating.
Two of object of the present invention is, a kind of in-situ authigenic advanced composite material coating of the surface abrasion resistance antifriction intensive treatment for non-ferrous metal cold deformation die for processing is provided, and realizes the surface abrasion resistance antifriction intensive treatment of mould.
Three of object of the present invention is to provide a kind of transferred plasma arc the deposited method of preparing in-situ authigenic advanced composite material coating.
The invention discloses a kind of (TiC+CaF
2)/γ-Ni in-situ authigenic abrasion-proof self-lubricating composite material coating and the deposited preparation method of transferred plasma arc thereof.This coating main chemical compositions is: Ti (wt%) is 42.5～46.25, C (wt%) is 10.63～11.56, Ni (wt%) is 31.88～34.69, CaF
2(wt%) be 7.5～15.The Ni-based sosoloid of supersaturation and the CaF of coating Main Tissues forms a large amount of Ti that have been sintering metal phase TiC, solid solution mutually and C element
2solid lubrication phase.
The deposited technology of described transferred plasma arc, is characterized in that: the step that this technology is prepared composite coating is:
1) preparation powdered alloy, is specially: by granularity, be 80～320 object Ti powder, Ni powder, C powder and CaF
2powder is divided into three groups according to different mass score respectively, after 80 orders and the filtration of 150 object sieves, in mixer, fully mixes, and is then placed in loft drier and fully dries at 135 ℃.
2) open successively plasma electric source switch, control lathe switch, powder feeder switch; the transferred plasma arc of igniting; by following processing parameter, start the described coating of deposited preparation: working current 120A; operating voltage 30V; sweep velocity 1mm/s; synchronous powder feeding system amount 25～30g/min, shielding gas flow amount 2.4L/h, working gas flow 80L/h.
The deposited concrete technology of transferred plasma arc is: metal base is under high temperature high-energy-density transferred plasma arc heat effect, shallow-layer melts rapidly, meanwhile, through the hybrid alloys powder of drying, by working gas, be sent in transferred plasma arc post, powder is by high temperature high-energy-density transferred plasma arc rapid heating, fusing rapidly, the powdered alloy of fusing and the shallow-layer base material of fusing mix at substrate surface and form molten bath, under the stirring action of plasma beam, the raw metallurgical reaction of the abundant hybrid concurrency of each element in molten bath, after plasma beam is removed, owing to there being huge thermograde between molten bath and base material, under the heat conducting effect of base material, the quick nonequilibrium freezing in alloy molten bath, thereby obtain with base material and be good metallurgical binding, the deposited coating of fine microstructures, deposited concrete technology parameter is as implied above, whole deposited process is all the time in argon shield atmosphere.
Alloy weld pool solidifies is sequentially: at Ni-Ti-C-CaF
2in system, TiC has the highest fusing point and the most negative gibbs forms free energy, in alloy weld pool solidifies process, first TiC solidifies and separates out as primary phase, variation along with composition and temperature, most of surplus alloy molten solution solidifies and separates out with the form of the Ni-based sosoloid of γ-Ni supersaturation, in Ni-based sosoloid solid solution a large amount of Ti and C elements, the CaF that content is minimum, fusing point is minimum
2to separate out with the form final set of Ni-based sosoloid formation divorced eutectic, be fine platy disperse and be distributed in Ni-based sosoloid.
The deposited equipment of described transferred-arc plasma is DRF-1 type plasma melting compress apparatus.
Described metal matrix material is for manufacturing extrusion mould common used material Cr12MoV cold-work die steel.
Described (TiC+CaF
2)/γ-Ni in-situ authigenic abrasion-proof self-lubricating composite material coating, its chemical composition is: Ti (wt%) is 45～46.25, C (wt%) is 11.25～11.56, Ni (wt%) is 33.75～34.69, CaF
2(wt%) be 7.5～10.It is TiC, CaF mutually that coating Main Tissues forms
2and γ-Ni.
Described (TiC+CaF
2)/γ-Ni in-situ authigenic abrasion-proof self-lubricating composite material coating, its chemical composition is: Ti (wt%) is 43.75～45, C (wt%) is 10.94～11.25, Ni (wt%) is 32.81～33.75, CaF
2(wt%) be 10～12.5.It is TiC, CaF mutually that coating Main Tissues forms
2and γ-Ni.
Described (TiC+CaF
2)/γ-Ni in-situ authigenic abrasion-proof self-lubricating composite material coating, its chemical composition is: Ti (wt%) is 42.5～43.75, C (wt%) is 10.63～10.94, Ni (wt%) is 31.88～32.81, CaF
2(wt%) be 12.5～15.It is TiC, CaF mutually that coating Main Tissues forms
2and γ-Ni.
Due to CaF
2density is lower, particle diameter is less, in the process of carrying in the transferred plasma arc post of high temperature high-energy-density, and part CaF
2powder can scatter and disappear.In the present invention, CaF in mixed powder
2massfraction lower than 7.5% time, in coating, can't detect CaF
2phase; CaF in mixed powder
2massfraction higher than 7.5% lower than 15% time, in coating, there is CaF
2; CaF in mixed powder
2massfraction higher than 15% time, too much CaF
2affected coating forming quality.Therefore, the present invention is for the preparation of described (TiC+CaF
2caF in the powder raw material of)/γ-Ni in-situ authigenic abrasion-proof self-lubricating composite material coating
2high-content (wt%) be no more than 15%.
Beneficial effect
The invention discloses a kind of (TiC+CaF
2)/γ-Ni in-situ authigenic abrasion-proof self-lubricating composite material coating and the deposited preparation method of transferred plasma arc thereof, for having established theory and technical foundation the work-ing life that adopts economy, effective means to increase substantially non-ferrous metal cold deformation die for processing.
The present invention has overcome the deficiency of conventional die surface modification technology, and prepared coating and base material are good metallurgical binding, has excellent wear-resisting and antifriction performance.Its major advantage is:
First, powdered alloy is sent in arc column by working gas, powder is through high temperature high-energy-density line instant heating, rapid melting, the powder of fusing and the shallow-layer base material of fusing mix at substrate surface and form molten bath, the raw metallurgical reaction of the abundant hybrid concurrency of each element under the stirring action of plasma beam in molten bath, there is quick nonequilibrium freezing in molten bath subsequently under the heat conducting effect of base material, acquisition is the deposited coating of good metallurgical binding with base material, can guarantee when coating is on active service under the bad working environments of the strong wearing and tearing of high contact stress not come off, do not ftracture.
The second, coating wild phase TiC and self-lubricating phase CaF
2disperse is distributed on γ-Ni matrix, and the average hardness of coating is up to more than HV1600, and frictional coefficient is low and stable, coating has excellent wear-resisting and antifriction performance, for die surface modification, can effectively improve surface abrasion resistance and the antifriction performance of mould, increase substantially its work-ing life.
The 3rd, DRF-1 type plasma cladding system and the novel plasma torch of employing independent development, equipment manufacturing cost is lower, easy and simple to handle, production efficiency, powdered alloy utilization ratio is high, and coating preparation cost is reduced greatly.
Accompanying drawing explanation
Fig. 1 is 1
#the X ray diffracting spectrum of coating;
Fig. 2 is 2
#the X ray diffracting spectrum of coating;
Fig. 3 is 3
#the X ray diffracting spectrum of coating;
Fig. 4 is (TiC+CaF
2)/γ-Ni coating typical microstructures low power SEM photo;
Fig. 5 is (TiC+CaF
2)/γ-Ni coating typical microstructures high power SEM photo;
Fig. 6 is (TiC+CaF
2the microhardness distribution curve of)/γ-Ni coating;
Fig. 7 is (TiC+CaF
2the friction coefficient wearing-in period variation relation curve of)/γ-Ni coating;
Embodiment
The present invention is a kind of (TiC+CaF that utilizes the deposited technology of transferred plasma arc to prepare
2)/γ-Ni in-situ authigenic abrasion-proof self-lubricating composite material coating.The chemical composition of coating is: Ti (wt%) is 42.5～46.25, C (wt%) is 10.63～11.56, Ni (wt%) is 31.88～34.69, CaF
2(wt%) be 7.5～15.The Ni-based sosoloid of supersaturation and the CaF of coating Main Tissues forms a large amount of Ti that have been sintering metal phase TiC, solid solution mutually and C element
2self-lubricating phase.Coating structure is evenly complete metallurgical binding, hardness high (more than average hardness HV1600) between tiny and base material, frictional coefficient is low and stable, and coating has excellent wear resistance and good antifriction quality, CaF in coating
2content is higher, and coating frictional coefficient is lower, and wear resistance is better.
Embodiment
Choose three typical case (TiC+CaF through optimization design in table 1
2)/γ-Ni in-situ authigenic abrasion-proof self-lubricating composite material coating is tested coating as embodiment.
Table 1:(TiC+CaF
2)/γ-Ni in-situ authigenic abrasion-proof self-lubricating composite material coating chemical composition
| Coating | Ti(wt％) | Ni(wt％) | C(wt％) | CaF 2(wt％) |
| 1 # | 45～46.25 | 33.75～34.69 | 11.25～11.56 | 7.5～10 |
| 2 # | 43.75～45 | 32.81～33.75 | 10.94～11.25 | 10～12.5 |
| 3 # | 42.5～43.75 | 31.88～32.81 | 10.63～10.94 | 12.5～15 |
Preparation method:
(1) taking precision is electronic balance weighing Ni powder, Ti powder, C powder, the CaF of 0.1mg
2powder, by the quality of table 1 regulation, than hybrid alloys powder, it is 60～320 orders that powder size requires;
(2) three groups of hybrid alloys powder are placed in loft drier, in 135 ℃ of environment, fully dry;
(3) select Cr12MoV as base material, utilize the deposited system of DRF-1 type transferred plasma arc, under argon shield condition, at substrate surface, prepare coating.
1, utilize the deposited technology of transferred plasma arc to prepare coating
Selecting granularity is the above-mentioned powdered alloy of 60～320 object, utilizes the deposited system of DRF-1 type transferred plasma arc, adopts synchronous powder feeding system mode, under the condition of argon shield, and preparation (TiC+CaF on Cr12MoV steel substrate
2)/γ-Ni in-situ authigenic abrasion-proof self-lubricating composite material coating.
Transferred plasma arc deposition techniques parameter is: working current 120A, operating voltage 30V, sweep velocity 1mm/s, synchronous powder feeding system amount 30g/min, shielding gas flow amount 2.4L/h, working gas flow 80L/h.
2, coating microstructure analyzes
Adopt Dmax-2200pc rotating anode X-ray diffractometer to carry out Analysis of components to coating, by the digital optical metallographic microscope of MDS type and QUANTA200FEG type field launch environment scanning electronic microscope, carry out coating microstructure's analysis and wear morphology observation respectively.
Fig. 1, Fig. 2, Fig. 3 are respectively 1
#, 2
#with 3
#the X ray diffracting spectrum of coating.X-ray diffraction analysis result shows: 1
#, 2
#with 3
#the tissue composition of coating is TiC and γ-Ni and CaF mutually
2, wherein 3
#caF in coating
2the intensity of diffraction peak apparently higher than 2
#coating, more higher than 1
#coating, shows with CaF in mixed powder
2content increase, CaF in coating
2content also correspondingly increases.
Fig. 4 is the deposited (TiC+CaF of transferred plasma arc
2)/γ-Ni composite coating typical microstructures low power SEM photo.Visible, coating typical microstructures constitutional features is that the disperse of irregular block TiC primary phase is distributed in γ-Ni solid solution matrix, and through image analysis software measuring and calculating, the volume fraction of TiC primary phase is up to 82%.Fig. 5 is coating typical microstructures high power SEM photo, visible, disperse a small amount of fine platy CaF that distributing in γ-Ni solid solution matrix
2.
3, coating microhardness test
Utilizing the digital microhardness tester of MH-5L type to measure coating microhardness distributes.As shown in Figure 6, the Hardness Distribution of coating is high and more even for coating microhardness distribution curve, and average microhardness is all higher than HV1600, with increase and the CaF of TiC content in coating
2the reduction of content, coating hardness is the trend increasing gradually.
4, coating room temperature dry sliding wear experiment
On pin-disc type wear testing machine, carry out the experiment of room temperature dry sliding wear, coated material is of a size of 6mm * 8mm * 10mm, (quenching-low-temperaturetempering is processed with beating steel GCr15, hardness HRC62 ± 3) mill is rubbed, cause specimen surface to wear and tear, wear test parameter is as shown in table 2.
Table 2: skimming wear experiment parameter
| Load (N) | To bull ring speed of rotation (rpm) | Wearing-in period (min) |
| 172 | 300 | 40 |
With stainless steel 1Cr8Ni9Ti sample as a comparison, adopt weighting method to measure the wear weight loss of control sample and wearing and tearing sample, before and after wearing and tearing, all with alcohol, clean sample, by precision, be 10
-4gram electronic analytical balance weigh sample wear weight loss, use relative wear resistance ε
rbeing that standard specimen is weightless weighs sample wear resistance standard just, ε with being compared to of sample weightlessness
rlarger, represent that material wear ability is better.The wear test result of heterogeneity coating sample is as shown in table 3.
Table 3:(TiC+CaF
2)/γ-Ni coating room temperature dry sliding wear experimental result
| Specimen coding | Sample original weight (milligram) | Sample eventually heavy (milligram) | Weightless (milligram) | Relative wear resistance ε r |
| 1Cr8Ni9Ti | 4217.3 | 4164.6 | 52.7 | 1.0 |
| 1 #Coating | 4196.2 | 4181.7 | 14.5 | 36.3 |
| 2 #Coating | 3805.9 | 3803.9 | 2.0 | 26.3 |
| 3 #Coating | 3641.8 | 3634.9 | 6.9 | 7.6 |
As can be seen from Table 3, the deposited (TiC+CaF of transferred plasma arc
2)/γ-Ni composite coating has excellent wear-resisting and antifriction performance, with self-lubricating phase CaF in coating
2content increases, and coating abrasion performance is the trend increasing gradually and coating frictional coefficient is the trend reducing gradually.
Finally it should be noted that: obviously, above-described embodiment is only for the application's example is clearly described, and the not restriction to embodiment.For those of ordinary skill in the field, can also make other changes in different forms on the basis of the above description.Here exhaustive without also giving all embodiments.And the apparent variation of being amplified out thus or change are still among the protection domain in the application's type.
Claims (6)
1. (a TiC+CaF
2)/γ-Ni composite coating, is characterized in that: the powder raw material of preparing this composite coating comprises Ti powder, Graphite Powder 99, Ni powder and CaF
2powder, wherein Ti is that 42.5～46.25wt%, graphite are that 10.63～11.56wt%, Ni are 31.88～34.69wt%, CaF
2be 7.5～15wt%.The Ni-based sosoloid of supersaturation and the CaF of coating Main Tissues the forms Ti that has been sintering metal phase TiC, solid solution mutually and C element
2self-lubricating phase.
2. composite coating according to claim 1, is characterized in that: the chemical composition of described coating is that Ti is that 45～46.25wt%, graphite are that 11.25～11.56wt%, Ni are 33.75～34.69wt%, CaF
2be 7.5～10wt%.
3. composite coating according to claim 1, is characterized in that: the chemical composition of described coating is that Ti is that 43.75～45wt%, graphite are that 10.94～11.25wt%, Ni are 32.81～33.75wt%, CaF
2be 10～12.5wt%.
4. composite coating according to claim 1, is characterized in that: the chemical composition of described coating is that Ti is that 42.5～43.75wt%, graphite are that 10.63～10.94wt%, Ni are 31.88～32.81wt%, CaF
2be 12.5～15wt%.
5. utilize the deposited technology of transferred plasma arc to prepare a method for composite coating described in claim 1, it is characterized in that, comprise the steps:
(1) preparation powdered alloy, is specially: by granularity, be 80～320 object Ti powder, Ni powder, Graphite Powder 99 and CaF
2powder is divided into three groups according to different mass score respectively.First group: Ti is that 45～46.25wt%, graphite are that 11.25～11.56wt%, Ni are 33.75～34.69wt%, CaF
2be 7.5～10wt%; Second group: Ti is that 43.75～45wt%, graphite are that 10.94～11.25wt%, Ni are 32.81～33.75wt%, CaF
2be 10～12.5wt%; The 3rd group, Ti is that 42.5～43.75wt%, graphite are that 10.63～10.94wt%, Ni are 31.88～32.81wt%, CaF
2be 12.5～15wt%, after 80 orders and the filtration of 150 object sieves, in mixer, fully mix, be then placed in loft drier and fully dry at 135 ℃;
(2) utilize the deposited equipment of transferred plasma arc on metal base, to prepare coating, be specially, after striking, produce high temperature high-energy-density transferred plasma arc, metal base is under the rapid heating effect of plasma arc, shallow-layer melts rapidly, simultaneously, the powdered alloy of drying in step (1) is sent in plasma column by working gas, powdered alloy is heated to rapidly fusing by plasma arc, the powder of fusing and the shallow-layer base material of fusing mix at substrate surface and form molten bath, under the stirring action of plasma arc, each element in molten bath fully mixes, diffusion mutually, and there is metallurgical reaction, after plasma arc is removed, owing to there being huge thermograde between molten bath and base material, under the heat conducting effect of base material, alloy molten bath produces quick nonequilibrium freezing, thereby acquisition fine microstructures, with base material, be good metallurgical binding, the TiC sintering metal of coming into being of take is wear-resisting wild phase mutually, with solid solution a large amount of Ti, the Ni-based sosoloid of supersaturation of C is matrix, the fine platy CaF distributing with disperse
2for the in-situ authigenic abrasion-proof self-lubricating composite material coating of solid lubrication phase, in deposited process, alloy molten bath is subject to argon shield all the time, has avoided airborne oxygen, nitrogen to enter molten bath and has participated in reaction, causes the generation of oxide compound and nitride impurity phase.
6. method according to claim 5, is characterized in that: the deposited equipment of described transferred-arc plasma is the deposited system of DRF-1 type transferred plasma arc; Described transferred plasma arc deposition techniques parameter is: working current 120A, operating voltage 30V, sweep velocity 1mm/s, synchronous powder feeding system amount 25～30g/min, shielding gas flow amount 2.4L/h, working gas flow 80L/h; Described metal matrix material is Cr12MoV steel.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201410196052.0A CN104195493A (en) | 2014-05-09 | 2014-05-09 | A (TiC+CaF2)/gamma-Ni composite material coating and a plasma transferred arc deposition preparing method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201410196052.0A CN104195493A (en) | 2014-05-09 | 2014-05-09 | A (TiC+CaF2)/gamma-Ni composite material coating and a plasma transferred arc deposition preparing method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN104195493A true CN104195493A (en) | 2014-12-10 |
Family
ID=52080854
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201410196052.0A Pending CN104195493A (en) | 2014-05-09 | 2014-05-09 | A (TiC+CaF2)/gamma-Ni composite material coating and a plasma transferred arc deposition preparing method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN104195493A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109465461A (en) * | 2019-01-02 | 2019-03-15 | 西迪技术股份有限公司 | A kind of tungsten carbide stiff dough anti-friction bearing and preparation method thereof |
| CN110218889A (en) * | 2019-06-05 | 2019-09-10 | 北京交通大学 | A kind of Ti5Si3+CaF2Enhance in-situ authigenic multiphase doped and compounded material and preparation method thereof |
| CN110983287A (en) * | 2019-10-21 | 2020-04-10 | 武汉大学 | Method for transferring large-area two-dimensional materials |
| CN112609156A (en) * | 2020-11-20 | 2021-04-06 | 江苏科技大学 | Wide-temperature-range self-lubricating film material with thermal cycle service capacity and preparation method thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4731253A (en) * | 1987-05-04 | 1988-03-15 | Wall Colmonoy Corporation | Wear resistant coating and process |
| CN103205622A (en) * | 2013-04-01 | 2013-07-17 | 武汉理工大学 | TiAl-Ag-WS2-ZnO-Ti2AlC-TiC self-lubricating composite material and preparation method thereof |
-
2014
- 2014-05-09 CN CN201410196052.0A patent/CN104195493A/en active Pending
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4731253A (en) * | 1987-05-04 | 1988-03-15 | Wall Colmonoy Corporation | Wear resistant coating and process |
| CN103205622A (en) * | 2013-04-01 | 2013-07-17 | 武汉理工大学 | TiAl-Ag-WS2-ZnO-Ti2AlC-TiC self-lubricating composite material and preparation method thereof |
Non-Patent Citations (3)
| Title |
|---|
| 孙晓夏: "《实用阀门技术问答（第二版）》", 31 May 2008, article "合金粉末" * |
| 张欣: "连续挤压模具等离子体材料表面改性研究", 《中国优秀硕士学位论文全文数据库（电子期刊）工程科技Ⅰ辑》, 15 May 2013 (2013-05-15) * |
| 韦福水等: "《热喷涂技术》", 31 December 1986, article "合金粉末" * |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109465461A (en) * | 2019-01-02 | 2019-03-15 | 西迪技术股份有限公司 | A kind of tungsten carbide stiff dough anti-friction bearing and preparation method thereof |
| CN110218889A (en) * | 2019-06-05 | 2019-09-10 | 北京交通大学 | A kind of Ti5Si3+CaF2Enhance in-situ authigenic multiphase doped and compounded material and preparation method thereof |
| CN110983287A (en) * | 2019-10-21 | 2020-04-10 | 武汉大学 | Method for transferring large-area two-dimensional materials |
| CN112609156A (en) * | 2020-11-20 | 2021-04-06 | 江苏科技大学 | Wide-temperature-range self-lubricating film material with thermal cycle service capacity and preparation method thereof |
| CN112609156B (en) * | 2020-11-20 | 2023-09-12 | 江苏科技大学 | Wide-temperature-range self-lubricating film material with thermal cycle service capability and preparation method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| Güler et al. | The wear and arc erosion behavior of novel copper based functionally graded electrical contact materials fabricated by hot pressing assisted electroless plating | |
| Liu et al. | Effects of La2O3 on microstructure and wear properties of laser clad γ/Cr7C3/TiC composite coatings on TiAl intermatallic alloy | |
| CN103540790B (en) | A kind of preparation method of anti-corrosion CuAlCr laser melting coating layer material | |
| CN102899664A (en) | Laser cladding alloy powder and preparation method thereof | |
| CN102719708A (en) | Laser-cladding high-toughness high-hardness nickel-base alloy powder and preparation method thereof | |
| CN106756717B (en) | Preparation method of high-strength wear-resistant copper-nickel-tin alloy coating | |
| CN106191853A (en) | A kind of wear resistant friction reducing cermet composite coating technique of hot die steel | |
| Wang et al. | Effect of the content of ball-milled expanded graphite on the bending and tribological properties of copper–graphite composites | |
| CN102962447A (en) | Titanium carbide metal ceramic powder and method for laser cladding of powder | |
| CN104195493A (en) | A (TiC+CaF2)/gamma-Ni composite material coating and a plasma transferred arc deposition preparing method thereof | |
| Wang et al. | Microstructural, mechanical and tribological performances of carbon fiber reinforced copper/carbon composites | |
| CN102691024B (en) | Copper-molybdenum disulfide self-lubricating conductive coating and preparation method thereof | |
| CN106521250A (en) | Novel large-current-carrying heat-resistant aluminum alloy wire and preparation method thereof | |
| CN107629832A (en) | A kind of hot extrusion glass lubricant of titanium alloy and zircaloy and preparation method thereof | |
| CN104480461A (en) | Laser cladding method for Cr12MoV steel through multiple overlapping of Ni60/SiC composite powder | |
| Cao et al. | Tribological and mechanical behaviors of engine bearing with CuSn10 layer and h-BN/graphite coating prepared by spraying under different temperatures | |
| CN113293370A (en) | High-entropy alloy coating for laser cladding of aluminum alloy surface and preparation method | |
| CN102266944A (en) | Method for preparing SiC grain enhanced Cu-base gradient compound material | |
| Liu et al. | Microstructure and properties of silver-added W-Cu prepared by infiltration sintering | |
| CN103307109B (en) | A kind of preparation method of abrasion-proof bearing bush | |
| CN104232999A (en) | Wear-resistant zinc alloy and forming method thereof | |
| CN111979539A (en) | Copper-based amorphous composite coating and preparation method thereof | |
| CN109112461A (en) | A kind of method that laser two-step method prepares aluminium-based amorphous alloy composite ceramic coat in ocean platform steel surface | |
| CN103042209B (en) | Nano silicon carbide and nano cerium oxide synergetically enhanced metal matrix micro-nano powder and preparing method thereof | |
| CN106702306B (en) | A kind of TiC enhancing high-temperature alloy base high-temperature wear-resistant composite material and preparation method |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20141210 |
|
| RJ01 | Rejection of invention patent application after publication |