CN104005019A - Preparation method of aluminum alloy surface composite coating layer - Google Patents
Preparation method of aluminum alloy surface composite coating layer Download PDFInfo
- Publication number
- CN104005019A CN104005019A CN201410176571.0A CN201410176571A CN104005019A CN 104005019 A CN104005019 A CN 104005019A CN 201410176571 A CN201410176571 A CN 201410176571A CN 104005019 A CN104005019 A CN 104005019A
- Authority
- CN
- China
- Prior art keywords
- powder
- aluminum alloy
- laser
- nicral
- tic
- 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
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 52
- 238000002360 preparation method Methods 0.000 title claims abstract description 12
- 239000002131 composite material Substances 0.000 title abstract description 4
- 239000011247 coating layer Substances 0.000 title abstract 4
- 230000008018 melting Effects 0.000 claims abstract description 26
- 238000002844 melting Methods 0.000 claims abstract description 25
- 238000012545 processing Methods 0.000 claims abstract description 4
- 239000000843 powder Substances 0.000 claims description 106
- 238000005253 cladding Methods 0.000 claims description 65
- 238000000576 coating method Methods 0.000 claims description 64
- 239000011248 coating agent Substances 0.000 claims description 62
- 150000001875 compounds Chemical class 0.000 claims description 46
- 239000000463 material Substances 0.000 claims description 23
- 229910052782 aluminium Inorganic materials 0.000 claims description 15
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 claims description 12
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 6
- 239000012535 impurity Substances 0.000 claims description 6
- 238000005480 shot peening Methods 0.000 claims description 6
- 238000000034 method Methods 0.000 abstract description 32
- 239000002245 particle Substances 0.000 abstract description 24
- 230000008569 process Effects 0.000 abstract description 12
- 239000011148 porous material Substances 0.000 abstract description 4
- 239000000758 substrate Substances 0.000 abstract description 4
- 230000008901 benefit Effects 0.000 abstract description 3
- 230000004048 modification Effects 0.000 abstract description 3
- 238000012986 modification Methods 0.000 abstract description 3
- 239000002103 nanocoating Substances 0.000 abstract description 3
- 238000010521 absorption reaction Methods 0.000 abstract description 2
- 230000007547 defect Effects 0.000 abstract description 2
- 239000012895 dilution Substances 0.000 abstract description 2
- 238000010790 dilution Methods 0.000 abstract description 2
- 239000011858 nanopowder Substances 0.000 abstract description 2
- 239000010410 layer Substances 0.000 abstract 2
- 229910045601 alloy Inorganic materials 0.000 description 13
- 239000000956 alloy Substances 0.000 description 13
- 238000004372 laser cladding Methods 0.000 description 9
- 230000004580 weight loss Effects 0.000 description 8
- 230000000694 effects Effects 0.000 description 7
- 238000005260 corrosion Methods 0.000 description 5
- 208000037656 Respiratory Sounds Diseases 0.000 description 4
- 229910010413 TiO 2 Inorganic materials 0.000 description 4
- 238000010276 construction Methods 0.000 description 4
- 239000013078 crystal Substances 0.000 description 4
- 239000002086 nanomaterial Substances 0.000 description 4
- 238000012876 topography Methods 0.000 description 4
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 239000002105 nanoparticle Substances 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 238000005299 abrasion Methods 0.000 description 2
- 239000004411 aluminium Substances 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 230000007812 deficiency Effects 0.000 description 2
- 239000000428 dust Substances 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 229910018125 Al-Si Inorganic materials 0.000 description 1
- 229910018520 Al—Si Inorganic materials 0.000 description 1
- 229910000676 Si alloy Inorganic materials 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- 238000002679 ablation Methods 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- CSDREXVUYHZDNP-UHFFFAOYSA-N alumanylidynesilicon Chemical compound [Al].[Si] CSDREXVUYHZDNP-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 235000013339 cereals Nutrition 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 239000007771 core particle Substances 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000032798 delamination Effects 0.000 description 1
- 238000004134 energy conservation Methods 0.000 description 1
- 238000003912 environmental pollution Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 235000013312 flour Nutrition 0.000 description 1
- 238000007306 functionalization reaction Methods 0.000 description 1
- 238000007373 indentation Methods 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- 238000010309 melting process Methods 0.000 description 1
- 238000003801 milling Methods 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 231100000289 photo-effect Toxicity 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 239000011863 silicon-based powder Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000007751 thermal spraying Methods 0.000 description 1
- 230000003245 working effect Effects 0.000 description 1
Abstract
The invention discloses a preparation method of an aluminum alloy surface composite coating layer, and belongs to the laser processing technical field. An NiCrAl/TiC nano coating layer is prepared on the surface of an aluminum alloy through melting covering by using a CO2 high-power laser device; a nano powder has small particle size and large specific surface area, and surface atoms are in an unstable state, so that a melting point is relatively low, the absorption rate on CO2 laser is relatively large, the laser energy density required in the melting covering process is also relatively small, and thus the dilution rate of the coating layer on a substrate can be guaranteed to be relatively small. The interior of the melting-covered layer prepared by the method is free of cracks, pores and other defects; and the prepared laser melting-covered coating layer is suitable for the remanufacturing technical fields such as surface modification and repairing of aluminum alloy engines and other structural parts, can greatly improve the usability of the aluminum alloy structural parts, prolongs the service life, and achieves great economic benefits.
Description
Technical field
The preparation method who the present invention relates to a kind of aluminum alloy surface compound coating, belongs to technical field of laser processing.
Background technology
Density is little, specific tenacity is high owing to having for aluminium alloy, anti-corrosion and good moldability, the advantage such as with low cost and be widely applied in fields such as boats and ships, vehicle and aerospace.Particularly in recent decades, world energy sources crisis and environmental pollution become the ultimate challenge of automobile industry, and automotive energy-saving emission-reducing intensity strengthens, lightweight process is accelerated, thereby caused aluminium alloy car structural part ratio constantly to increase.But aluminium alloy exists surface hardness low, frictional coefficient is high, wearing and tearing are large, easily pulls and is difficult to and lubricate, and the deficiencies such as the low easy generation viscous deformation of intensity, make it as important structure part, under severe military service operating mode, easily produce and lose efficacy.Common invalidation has: rooved face wearing and tearing and fatigure failure for compression ring, and pull skirt of piston, and cylinder lid surface annular indentation and planeness are overproof, engine-mounting bracket fracture etc.These intrinsic deficiencies have limited the further broader applications of aluminium alloy engine structural part to a great extent.With respect to Aluminium Alloys in Common Use surface modifying method, laser melting coating can utilize high-energy-density laser beam that high-melting-point powder melting is formed to the cladding compound coating with metallurgical binding at low melting point substrate surface, high, the wear-resisting and corrosion resistance excellent of the coating hardness of preparation.Therefore, in aluminum alloy surface preparation, be combined good wear-resisting, laser melting and coating technique anti-corrosion compound coating with alloy matrix aluminum in recent years and be subject to investigator's favor.
The thermal conductivity of aluminium alloy is good, and when aluminum alloy surface is carried out laser melting coating, weld pool solidifies speed is exceedingly fast, and the inner residual tension of cladding layer after solidifying is larger, easily cracks.Patent CN102373469A has announced a kind of method of inhibiting laser cladding layer cracks through continuous mechanical vibration, the method is auxiliary low frequency high amplitude mechanical vibration in laser cladding process, make grain refining, be conducive to discharge molten bath internal residual stress simultaneously, reach the effect of less cladding layer internal fissure.But the method can only effectively reduce crack number, and can not fundamentally eliminate crackle.Patent CN102383126A has announced a kind of have preheating and after heat function and efficient three beam laser cladding flawless coating productions, the laser beam that the method adopts laser beam splitter mirror that Nd:YAG laser apparatus is sent is divided into two bundle laser, beam of laser is preheating laser beam, and another beam of laser is after heat laser beam.Using CO
2laser beam carries out preheating and postheat treatment with these two kinds of laser beams to sample respectively while carrying out cladding experiment, and the cladding layer flawless of preparing produces.The shortcoming of the method is that equipment and process is more numerous and diverse, and preheating simultaneously and after heat laser beam power regulate wayward.
Aluminium alloy is to CO
2the uptake factor of laser apparatus is extremely low, and the laser cladding powder particle diameter overwhelming majority is micron order (> 1 μ m) at present, for simultaneously melted alloy powder and substrate surface, obtain being combined with base material good cladding layer, must improve laser power density, yet the fusing point of aluminium alloy lower (being about 660 ℃), under high power density, the thinning ratio of cladding layer is higher.In patent CN102534467A, announced a kind of method of preparing high silicon content coating at ZL 101 alloy surface laser cladding, powder size 74 μ m in the method.45 ~ 100 μ m) and SiC powder (granularity: 75 μ m) patent CN101012561A has announced a kind of Alloy Cladding on Al Surface by Laser enhancement method, and powder used is respectively Al-Si powder (granularity:.Patent CN1537970A has announced the manufacture method of a kind of aluminium alloy engine spare part laser alloying, and the powder diameter scope adopting in the method is 70 μ m ~ 200 μ m.In above several method, powder size is all larger, needs higher laser energy to carry out melting powder, causes coating thinning ratio higher.Therefore,, when aluminum alloy surface is carried out laser melting coating modification, adopt nanoscale powder just to become and solve the desired solution that cladding layer ftractures and reduces thinning ratio.
Since Xu Bin scholar academician in 1997 proposes the concept of " nano surface work ", take " nano surface work technology " that " nanotechnology " be core obtained the great attention of domestic scholars.Nanometer powder surface atom state labile, lattice surface amplitude is larger, has higher surface energy, can cause nanometer powder melting point depression.Meanwhile, nano particle diameter (< 100 nm) is less than CO
2laser beam wavelength (10.6 μ m), nanoparticle can with CO
2laser beam produces complicated interaction, thereby greatly improves the specific absorption to incident light.Due to the special thermal properties of nanometer powder and light property, for the raising of nanocoating performance provides favourable condition.Research shows, compares with conventional coatings, and nano-structured coating is significantly improved at aspects such as intensity, toughness, against corrosion, wear-resisting, thermal boundary, thermal fatigue resistances.Application of nanopowder, in surface laser cladding surface modification field, is prepared to the surface fused coating that contains nanostructure, can make the mechanics of substrate surface, physics and chemistry performance improve, reach the object that material surface modifying combines with functionalization.
Zhang Guangjun etc. prepare nanometer Al at < < cast aluminium surface laser
2o
3/ TiO
2the Wear Resistance > > mono-of coating the article pointed out, is selecting under abrasive conditions cast aluminium ZL104 surface laser cladding nanometer (NF) Al
2o
3/ TiO
2the relative wear resistance of coating is than thermospray Al
2o
3/ TiO
2coating is significantly improved, and under similarity condition, the relative wear volume of the relative wear volume ratio thermospray of laser cladding layer has reduced 92%.This is because of the result of laser melting and coating process and nano material " nano effect " comprehensive action.But the method is being carried out laser melting coating Al
2o
3/ TiO
2before coating experiment, need to cause the method complex process at ZL104 aluminum alloy base material thermal spraying on surface Ni bag Al prime coat, efficiency is low.
Through to the periodical of publishing and patent retrieval, not yet find to prepare at aluminum silicon alloy surface laser cladding the method for nanostructure NiCrAl/TiC compound coating both at home and abroad.
Summary of the invention
The object of the invention be to provide a kind of simple and easy, efficiently, the preparation method of aluminum alloy surface compound coating cheaply, be specially a kind of Alloy Cladding on Al Surface by Laser surface modifying method, obtain high abrasion, anti-corrosion cladding modified layer, extend aluminum alloy junction member work-ing life, produce larger economic benefit.
The method of the invention specifically comprises the following steps:
(1) aluminum alloy plate materials is cut into laser melting coating sample, shot peening is carried out in the cladding surface of aluminum alloy plate materials sample;
(2) with acetone and alcohol, remove cladding specimen surface oxide compound, impurity and greasy dirt;
(3) NiCrAl powder and TiC powder is stand-by after dry 6 ~ 8h at 70 ~ 100 ℃;
(4) with crossing current multimode CO
2laser apparatus and supporting powder feeding equipment obtain the compound coating of aluminum alloy surface by NiCrAl powder and TiC powder melting at aluminum alloy plate materials sample.
Described in step of the present invention (3), the powder size of NiCrAl powder and TiC is 60 ~ 100 nm, wherein NiCrAl powder is to be mixed by Ni, the Cr of 60 ~ 100 nm, the powder of Al, in NiCrAl powder, the mass percent of Cr is 16% ~ 18%, the mass percent of Al is 6% ~ 8%, and remaining is Ni powder.
Described in step of the present invention (4), in compound coating, the massfraction of TiC is 0 ~ 30%.
Crossing current multimode CO in step of the present invention (4)
2the processing parameter of laser apparatus is: laser power 3.8 ~ 4.2kW, and sweep velocity 380 ~ 420 mm/min, NiCrAl powder feeding rate is 0.5 ~ 0.6g/s; TiC powder powder feeding rate is 0 ~ 0.26g/s; shielding gas flow speed 8 ~ 10 L/h, defocusing amount 40 ~ 45mm, spot diameter is 5 ~ 6mm.
In step of the present invention (4), the thickness of compound coating is 1.0 ~ 2.0 mm, and width is 4 ~ 5 mm.
In step of the present invention (4), can adopt the powder feeding equipment of multichannel powder feeding function to carry out powder feeding, every road powder sending quantity can be realized independent control.
Principle of the present invention is: utilize the laser beam of high-energy-density to melt NiCrAl powder and TiC powder simultaneously, and make melted powder and the micro-molten aluminum alloy base material in surface reach the cladding layer of metallurgical binding feature; The powder size adopting due to present method is nano level, and under the condition of laser melting coating rapid heat cycle, the weave construction obtaining belongs to nanostructure; The TiC particle adding, because fusing point is higher, can preferentially be separated out in cladding layer process of setting, plays the effect of heterogeneous forming core, thereby makes the weave construction refinement more of cladding layer; The weave construction of refinement is conducive to the raising of cladding layer wear resisting property.
Beneficial effect of the present invention:
(1) powder used in the present invention is nanoscale powder, the obvious refinement of microstructure of surface cladding layer structure, the defects such as cladding layer flawless and pore, due to the special heat effect of nanometer powder and photoeffect, thereby can reduce power density, reduce the dilution of cladding layer to base material, simultaneously, because the fusing point of nanometer is low, absorptivity is high, in experimentation, energy conservation rate improves more than 1 times;
(2) the present invention adds nano-TiC particle in NiCrAl powder, and nano TiC strengthens and when metal-base composites is joined pair with metal, to have lower frictional coefficient (compare with plus nano TiC not, frictional coefficient reduces 10% ~ 20%); Meanwhile, the refined crystalline strengthening effect of nano-TiC particle has compared with the better abrasion resistance properties of nanometer NiCrAl powder (compare with plus nano TiC not, wear resistance improves 22% ~ 37%) cladding layer.
Accompanying drawing explanation
To be the present invention prepare particle diameter in Alloy Cladding on Al Surface by Laser to Fig. 1 is 60 figure of nm NiCrAl compound coating displaing micro tissue topographies;
To be the present invention prepare particle diameter in Alloy Cladding on Al Surface by Laser to Fig. 2 is respectively 80 nm NiCrAl and the figure of 80 nmTiC compound coating displaing micro tissue topographies (TiC massfraction 15%);
To be the present invention prepare particle diameter in Alloy Cladding on Al Surface by Laser to Fig. 3 is respectively 100 nm NiCrAl and the figure of 100 nmTiC compound coating displaing micro tissue topographies (TiC massfraction 30%);
Fig. 4 is that Alloy Cladding on Al Surface by Laser of the present invention is prepared particle diameter and is respectively the figure of 80 μ m NiCrAl and 80 μ m TiC compound coating displaing micro tissue topographies (TiC massfraction 15%);
Fig. 5 is that in Alloy Cladding on Al Surface by Laser, to prepare particle diameter be 60 nm NiCrAl compound coating wear morphologies in the present invention;
Fig. 6 is that the present invention prepares particle diameter in Alloy Cladding on Al Surface by Laser and is respectively 80 nm NiCrAl and 80 nm TiC compound coating wear morphologies (TiC massfraction 15%);
Fig. 7 is that the present invention prepares particle diameter in Alloy Cladding on Al Surface by Laser and is respectively 100 nm NiCrAl and 100 nm TiC compound coating wear morphologies (TiC massfraction 30%);
Fig. 8 is that Alloy Cladding on Al Surface by Laser of the present invention is prepared particle diameter and is respectively 80 μ m NiCrAl and 80 μ m TiC compound coating wear morphologies (TiC massfraction 15%).
Embodiment
Below in conjunction with drawings and Examples, the present invention is further elaborated, but protection domain of the present invention is not limited to described content.
Embodiment 1
(1) aluminum alloy plate materials is cut into laser melting coating sample, shot peening is carried out in the cladding surface of aluminum alloy plate materials sample;
(2) with acetone and alcohol, remove except cladding specimen surface oxide compound, impurity and greasy dirt;
(3) NiCrAl powder dry 8h at 70 ℃ is obtained to pretreated NiCrAl powder, wherein NiCrAl powder is to be mixed by Ni, the Cr of 60 nm, the powder of Al, in NiCrAl powder, the mass percent of Cr is 16%, the mass percent of Al is that the mass percent of 6%, Ni powder is 78%;
(4) with crossing current multimode CO
2laser apparatus obtains compound coating by NiCrAl powder melting at aluminum alloy plate materials sample; wherein; laser power 3.8 kW; sweep velocity 420 mm/min, NiCrAl powder feeding rate is 0.5 g/s, shielding gas flow speed 8L/h; defocusing amount 40 mm; spot diameter is 5mm, and the thickness of compound coating is 1.0 mm, and width is 4 mm.
The aluminum alloy surface compound coating that the present embodiment prepares as shown in Figure 1, as can be known from Fig. 1, the existence of nano particle has increased matrix metal nucleation rate, refinement cladding layer crystal grain, tissue is mainly tiny equiax crystal, and there are several equiax crystal connection growth phenomenons, grain-size is about 100 ~ 300 nm; Cladding layer good moldability, flawless and pore occur; Utilizing microhardness tester to measure cladding layer average microhardness is 676 HV
0.2; Fig. 5 is the wear morphology that this embodiment is corresponding, as we know from the figure, there is discontinuous, thin and shallow slight ditch dug with a plow in cladding layer surface, and this is because there are a large amount of hard particles in cladding layer, in wear process, under positive pressure and tangential friction force acting in conjunction, between cladding layer surface shallow-layer and hard particles and matrix, produce larger stress concentration, form formation of crack, constantly rubbing and rolling in process, crackle is constantly expanded, and causes that cladding layer generation scales off, and forms abrasive dust; In follow-up wear process, abrasive dust is mixed between flour milling, and cladding layer is had to certain ablation, produces a large amount of slight plow wearing and tearing on surface; Table 1 is the wear weight loss that the present embodiment is corresponding.
Table 1 cladding layer wear weight loss
| Time/(min) | 0-25 | 25-50 | 50-75 | 75-100 | 100-125 |
| Sample/(mg) | 2.05 | 3.70 | 4.75 | 6.50 | 8.40 |
Embodiment 2
(1) aluminum alloy plate materials is cut into laser melting coating sample, shot peening is carried out in the cladding surface of aluminum alloy plate materials sample;
(2) with acetone and alcohol, remove cladding specimen surface oxide compound, impurity and greasy dirt;
(3) by NiCrAl powder and TiC powder, dry 7h at 85 ℃ obtains pretreated NiCrAl powder and TiC powder, wherein, the powder size of NiCrAl powder and TiC is 80nm, wherein NiCrAl powder is to be mixed by Ni, the Cr of 80nm, the powder of Al, in NiCrAl powder, the mass percent of Cr is 17%, the mass percent of Al is that the mass percent of 7%, Ni powder is 76%;
(4) with crossing current multimode CO
2laser apparatus obtains compound coating by NiCrAl powder and TiC powder melting at aluminum alloy plate materials sample; wherein; laser power 4.0 kW, sweep velocity 400 mm/min, NiCrAl powder feeding rate is 0.55 g/s; TiC powder powder feeding rate is that in the compound coating that obtains of 0.1 g/s(, TiC content is 15%); shielding gas flow speed 9L/h, defocusing amount 42mm, spot diameter is 5.5mm; the thickness of compound coating is 1.5mm, and width is 4.5 mm.
As shown in Figure 2, there is the phenomenon of the raw growth of crystal grain connection in the aluminum alloy surface compound coating that the present embodiment prepares, grain-size is about 300 ~ 500 nm, there is no crackle and pore in cladding layer in weld pool solidifies process; At grain boundaries, found that particle diameter is about the tiny TiC particle of 100 nm, TiC particle fusing point is high, in weld pool solidifies process, can preferentially separate out, and as heterogeneous forming core particle, plays the effect of refined crystalline strengthening and second-phase strengthening; Utilizing microhardness tester to measure cladding layer average microhardness is 752.35 HV
0.2; Fig. 6 is the cladding layer worn surface that this embodiment is corresponding, and as we know from the figure, cladding layer surface is also mainly to take micro-cutting as main, and in cladding layer, the existence of TiC particle makes microstructure of surface cladding layer structure refinement simultaneously, makes the ditch dug with a plow of wear surface more carefully more shallow; Table 2 is the wear weight loss that the present embodiment is corresponding.
Table 2 cladding layer wear weight loss
| Time/(min) | 0-25 | 25-50 | 50-75 | 75-100 | 100-125 |
| Sample/(mg) | 1.65 | 3.05 | 3.84 | 5.20 | 6.55 |
Embodiment 3
(1) aluminum alloy plate materials is cut into laser melting coating sample, shot peening is carried out in the cladding surface of aluminum alloy plate materials sample;
(2) with acetone and alcohol, remove cladding specimen surface oxide compound, impurity and greasy dirt;
(3) by NiCrAl powder and TiC powder, dry 6h at 100 ℃ obtains pretreated NiCrAl powder and TiC powder, wherein, the powder size of NiCrAl powder and TiC is 100 nm, wherein NiCrAl powder is to be mixed by Ni, the Cr of 100 nm, the powder of Al, in NiCrAl powder, the mass percent of Cr is 18%, the mass percent of Al is that the mass percent of 8%, Ni is 74%;
(4) with crossing current multimode CO
2laser apparatus obtains compound coating by NiCrAl powder and TiC powder melting at aluminum alloy plate materials sample; wherein; laser power 4.2 kW, sweep velocity 380 mm/min, NiCrAl powder feeding rate is 0.6 g/s; TiC powder powder feeding rate is that in the compound coating that obtains of 0.26 g/s(, TiC content is 30%); shielding gas flow speed 10 L/h, defocusing amount 45mm, spot diameter is 6mm; the thickness of compound coating is 2.0mm, and width is 5 mm.
The compound coating that the present embodiment prepares aluminum alloy surface as shown in Figure 3, Composite Coating alligatoring, grain-size is about 500 ~ 600 nm; At grain boundaries, found black TiC particle, particle diameter is about 100 ~ 200 nm, and meanwhile, at the grain boundaries that contains TiC particle, grain-size will be compared with the obvious refinement in other positions; Utilizing microhardness tester to measure cladding layer average microhardness is 846.86 HV
0.2; Fig. 7 is the corresponding cladding layer wear morphology of this embodiment, and the ditch dug with a plow that wear surface produces is as we know from the figure indistinct, extremely unintelligible; This is because TiC content in this embodiment reaches 30%, has significantly improved cladding layer microhardness, and the polishing machine of this cladding layer is further promoted; Table 3 is the wear weight loss that the present embodiment is corresponding.
Table 3 cladding layer wear weight loss
| Time/(min) | 0-25 | 25-50 | 50-75 | 75-100 | 100-125 |
| Example 3 /(mg) | 1.21 | 2.43 | 3.05 | 4.17 | 5.26 |
Embodiment 4
(1) aluminum alloy plate materials is cut into laser melting coating sample, shot peening is carried out in the cladding surface of aluminum alloy plate materials sample;
(2) with acetone and alcohol, remove cladding specimen surface oxide compound, impurity and greasy dirt;
(3) by NiCrAl powder and TiC powder, dry 7h at 85 ℃ obtains pretreated NiCrAl powder and TiC powder, wherein, the powder size of NiCrAl powder and TiC is 80 μ m, wherein NiCrAl powder is to be mixed by Ni, the Cr of 80 μ m, the powder of Al, in NiCrAl powder, the mass percent of Cr is 17%, the mass percent of Al is that the mass percent of 7%, Ni is 76%;
(4) with crossing current multimode CO
2laser apparatus obtains compound coating by NiCrAl powder and TiC powder melting at aluminum alloy plate materials sample; wherein; laser power 4.0 kW, sweep velocity 400 mm/min, NiCrAl powder feeding rate is 0.55 g/s; TiC powder powder feeding rate is that in the compound coating that obtains of 0.1 g/s(, TiC content is 15%); shielding gas flow speed 9L/h, defocusing amount 42mm, spot diameter is 5.5mm; the thickness of compound coating is 1.5mm, and width is 4.5 mm.
The compound coating that the present embodiment prepares aluminum alloy surface as shown in Figure 4, as we know from the figure, in embodiment 4, weave construction is that born of the same parents' shape is brilliant, and occurs the phenomenon of the raw growth of the brilliant connection of a plurality of born of the same parents' shapes, powder diameter is large (>=100 μ m), the TiC particle that disperse is distributing large between born of the same parents' shape Jingjing; In Fig. 4 lower right, observing part crackle exists; With microhardness tester, measuring cladding layer average microhardness is 462.69 HV
0.2; Fig. 8 is the cladding layer worn surface that this embodiment is corresponding, and as we know from the figure, wear surface has produced larger area localized delamination phenomenon, this is because cladding layer surface hardness is low, in wear process, the secondary hard particle that rubs is embedded into cladding layer surface, produce serious plow effect.Table 4 is the wear weight loss that the present embodiment is corresponding.
Table 4 cladding layer wear weight loss
| Time/(min) | 0-25 | 25-50 | 50-75 | 75-100 | 100-125 |
| Sample/(mg) | 5.48 | 6.58 | 7.38 | 9.63 | 12.73 |
Claims (5)
1. a preparation method for aluminum alloy surface compound coating, is characterized in that, specifically comprises the following steps:
(1) aluminum alloy plate materials is cut into laser melting coating sample, shot peening is carried out in the cladding surface of aluminum alloy plate materials sample;
(2) with a kind of removal cladding specimen surface oxide compound, impurity and greasy dirt in acetone and alcohol;
(3) NiCrAl powder and TiC powder dry 6 ~ 8h at 70 ~ 100 ℃ is stand-by;
(4) with crossing current multimode CO
2laser apparatus and supporting powder feeding equipment obtain the compound coating of aluminum alloy surface by NiCrAl powder and TiC powder melting at aluminum alloy plate materials sample.
2. the preparation method of aluminum alloy surface compound coating according to claim 1, it is characterized in that: described in step (3), NiCrAl powder and TiC powder size are 60 ~ 100 nm, wherein NiCrAl powder is to be mixed by Ni, the Cr of 60 ~ 100 nm, the powder of Al, in NiCrAl powder, the mass percent of Cr is 16% ~ 18%, the mass percent of Al is 6% ~ 8%, and remaining is Ni powder.
3. the preparation method of aluminum alloy surface compound coating according to claim 1, is characterized in that: described in step (4), in compound coating, the massfraction of TiC is 0 ~ 30%.
4. the preparation method of aluminum alloy surface compound coating according to claim 1, is characterized in that: crossing current multimode CO in step (4)
2the processing parameter of laser apparatus is: laser power 3.8 ~ 4.2kW, and sweep velocity 380 ~ 420 mm/min, NiCrAl powder feeding rate is 0.5 ~ 0.6g/s; TiC powder powder feeding rate is 0 ~ 0.26g/s; shielding gas flow speed 8 ~ 10 L/h, defocusing amount 40 ~ 45mm, spot diameter is 5 ~ 6mm.
5. the preparation method of aluminum alloy surface compound coating according to claim 1, is characterized in that: in step (4), the thickness of compound coating is 1.0 ~ 2.0 mm, and width is 4 ~ 5 mm.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201410176571.0A CN104005019A (en) | 2014-04-29 | 2014-04-29 | Preparation method of aluminum alloy surface composite coating layer |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201410176571.0A CN104005019A (en) | 2014-04-29 | 2014-04-29 | Preparation method of aluminum alloy surface composite coating layer |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN104005019A true CN104005019A (en) | 2014-08-27 |
Family
ID=51365921
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201410176571.0A Pending CN104005019A (en) | 2014-04-29 | 2014-04-29 | Preparation method of aluminum alloy surface composite coating layer |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN104005019A (en) |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104347133A (en) * | 2014-09-10 | 2015-02-11 | 太原理工大学 | Preparing method of neutron absorbing plate for storage and transportation of nuclear fuel |
| CN104831124A (en) * | 2015-05-09 | 2015-08-12 | 芜湖鼎瀚再制造技术有限公司 | Ni-Cr-Al welding layer and preparation method thereof |
| CN104827197A (en) * | 2015-05-09 | 2015-08-12 | 安徽再制造工程设计中心有限公司 | Ni-Cr-Al nanometer welding layer for welding and preparation method thereof |
| CN105401146A (en) * | 2014-09-05 | 2016-03-16 | 通用汽车环球科技运作有限责任公司 | Laser cladding alloy for aluminum injection molds |
| CN106086988A (en) * | 2016-08-09 | 2016-11-09 | 天津工业大学 | A kind of laser melting coating closes the method for aluminium alloy anode oxide film |
| CN111621780A (en) * | 2020-05-28 | 2020-09-04 | 成都航空职业技术学院 | Method for preparing Al-Cr composite coating by laser cladding |
| WO2020220192A1 (en) * | 2019-04-29 | 2020-11-05 | Schaeffler Technologies AG & Co. KG | An aluminum alloy cage and a processing method of the aluminum alloy cage |
| CN112412287A (en) * | 2020-11-03 | 2021-02-26 | 泉州市派腾新材料科技有限公司 | Laser cladding-based heat-insulation composite fireproof door core and preparation method thereof |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103290402A (en) * | 2012-02-23 | 2013-09-11 | 财团法人工业技术研究院 | Method for providing protective and thermally conductive coatings |
-
2014
- 2014-04-29 CN CN201410176571.0A patent/CN104005019A/en active Pending
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103290402A (en) * | 2012-02-23 | 2013-09-11 | 财团法人工业技术研究院 | Method for providing protective and thermally conductive coatings |
Non-Patent Citations (6)
| Title |
|---|
| IVANOV, ET. AL.: "Physical nature of increasing strength of TiC-NiCrAl hard alloy surface layer by electron-beam irradiation", 《RARE METALS》, 30 October 2009 (2009-10-30) * |
| 刘午等: "NiAl基复合材料的研究进展", 《辽宁工程技术大学学报》, no. 04, 25 August 2005 (2005-08-25) * |
| 刘秀波等: "γ-TiAl金属间化合物合金激光表面合金化改性", 《稀有金属材料与工程》, no. 03, 25 June 2001 (2001-06-25) * |
| 唐守春等: "铝合金表面激光熔覆SiC/金属基复合涂层的组织与性能研究", 《应用激光》, no. 05, 25 October 1999 (1999-10-25) * |
| 欧阳洁等: "激光合成Ni-Cr-Al+12%TiC涂层的显微组织及耐磨性研究", 《材料导报》, 25 May 2007 (2007-05-25) * |
| 蔡利芳等: "铝合金激光表面改性技术研究进展", 《材料保护》, no. 10, 28 October 2006 (2006-10-28) * |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105401146A (en) * | 2014-09-05 | 2016-03-16 | 通用汽车环球科技运作有限责任公司 | Laser cladding alloy for aluminum injection molds |
| CN104347133A (en) * | 2014-09-10 | 2015-02-11 | 太原理工大学 | Preparing method of neutron absorbing plate for storage and transportation of nuclear fuel |
| CN104347133B (en) * | 2014-09-10 | 2015-09-09 | 太原理工大学 | A kind of preparation method of the neutron absorber plate for nuclear fuel storage transport |
| CN104831124A (en) * | 2015-05-09 | 2015-08-12 | 芜湖鼎瀚再制造技术有限公司 | Ni-Cr-Al welding layer and preparation method thereof |
| CN104827197A (en) * | 2015-05-09 | 2015-08-12 | 安徽再制造工程设计中心有限公司 | Ni-Cr-Al nanometer welding layer for welding and preparation method thereof |
| CN106086988A (en) * | 2016-08-09 | 2016-11-09 | 天津工业大学 | A kind of laser melting coating closes the method for aluminium alloy anode oxide film |
| CN106086988B (en) * | 2016-08-09 | 2017-12-19 | 天津工业大学 | A kind of method of laser melting coating closing aluminium alloy anode oxide film |
| WO2020220192A1 (en) * | 2019-04-29 | 2020-11-05 | Schaeffler Technologies AG & Co. KG | An aluminum alloy cage and a processing method of the aluminum alloy cage |
| CN111621780A (en) * | 2020-05-28 | 2020-09-04 | 成都航空职业技术学院 | Method for preparing Al-Cr composite coating by laser cladding |
| CN112412287A (en) * | 2020-11-03 | 2021-02-26 | 泉州市派腾新材料科技有限公司 | Laser cladding-based heat-insulation composite fireproof door core and preparation method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN104005019A (en) | Preparation method of aluminum alloy surface composite coating layer | |
| CN107253148B (en) | Combination method for forming gradient nano structure on surface layer of metal workpiece | |
| CN101736214B (en) | Light metal surface laser impact micronano particle injection reinforcing method | |
| CN102383126B (en) | Method with functions of preheating and postheating for forming crack-free coating with high efficiency by three-light-beam laser-cladding technique | |
| CN107034457B (en) | Spontaneous ceramic phase enhancing Fe based alloy cladding layer material of Laser Cladding in-situ and preparation method thereof | |
| CN102618870B (en) | Wear-resistant and abrasion-resistant mould and preparation process for forming protective coating on working surface of mould substrate | |
| CN106148949A (en) | A kind of laser-induction composite cladding Graphene strengthens Ni3the method of Ti composite | |
| CN102650029A (en) | Preparation method for nanometer ceramic composite coating material on surface of hot work die steel | |
| Vinod et al. | Effect of organic and inorganic reinforcement on tribological behaviour of aluminium A356 matrix hybrid composite | |
| CN108707894A (en) | Powder and process used in a kind of laser melting coating self-lubricating abrasion-resistant cobalt-base alloys | |
| CN105714235A (en) | TiO2-CNTs nano-composite powder for thermal spraying and preparing method for coating of TiO2-CNTs nano-composite powder | |
| CN106191853A (en) | A kind of wear resistant friction reducing cermet composite coating technique of hot die steel | |
| CN101532121B (en) | Technology for processing metal surface by arc spray melting | |
| CN105543838A (en) | Remanufacturing method for marine crankshaft | |
| CN103484811A (en) | Preparation method of metal oxide based inorganic composite coating | |
| CN101928939B (en) | FenWnC-Co(Y) alloy nano coating, preparation method thereof and application thereof | |
| CN109440049B (en) | Method for preparing amorphous aluminum coating by compounding electric arc spraying and laser remelting | |
| Chen et al. | Microstructure and properties of 6061/2A12 dissimilar aluminum alloy weld by laser oscillation scanning | |
| Lu et al. | WC nano-particle surface injection via laser shock peening onto 5A06 aluminum alloy | |
| CN102212819B (en) | Method for preparing surface aluminium-based composite material by impacting heavily and repetitively at high speed | |
| CN101824640B (en) | Reconstructing method of micro arc of metal surface | |
| Napitupulu et al. | Friction stir welding of aluminium alloy 6061-t651 | |
| CN1313643C (en) | Method for assembling nickel base nano WC/Co composite plating on stainless steel surface using laser | |
| CN105937002A (en) | Aluminum alloy material replacing QT600 roller and jet forming method of aluminum alloy material | |
| Zhou et al. | Microstructure, mechanical properties, and tribological properties of laser assisted cold sprayed CuCrZr coatings: Influences of laser power and laser position |
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 | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20140827 |