CN114807824A - Low-cost high-performance Fe-based ultrafine grain plasma cladding layer and preparation method thereof - Google Patents
Low-cost high-performance Fe-based ultrafine grain plasma cladding layer and preparation method thereof Download PDFInfo
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- 238000005253 cladding Methods 0.000 title claims abstract description 122
- 238000002360 preparation method Methods 0.000 title claims abstract description 12
- 239000000463 material Substances 0.000 claims abstract description 61
- 239000000843 powder Substances 0.000 claims abstract description 34
- 238000001816 cooling Methods 0.000 claims abstract description 33
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 33
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 31
- 238000005507 spraying Methods 0.000 claims abstract description 25
- 239000000758 substrate Substances 0.000 claims abstract description 23
- 238000000034 method Methods 0.000 claims abstract description 14
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 10
- 239000000956 alloy Substances 0.000 claims abstract description 10
- 239000000498 cooling water Substances 0.000 claims abstract description 10
- PNXOJQQRXBVKEX-UHFFFAOYSA-N iron vanadium Chemical compound [V].[Fe] PNXOJQQRXBVKEX-UHFFFAOYSA-N 0.000 claims abstract description 9
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 8
- 229910000628 Ferrovanadium Inorganic materials 0.000 claims abstract description 7
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 16
- 239000007789 gas Substances 0.000 claims description 14
- 229910052786 argon Inorganic materials 0.000 claims description 8
- 238000003466 welding Methods 0.000 claims description 5
- 230000001681 protective effect Effects 0.000 claims description 4
- 239000011230 binding agent Substances 0.000 claims description 3
- 239000002245 particle Substances 0.000 claims description 3
- 235000019353 potassium silicate Nutrition 0.000 claims description 3
- NTHWMYGWWRZVTN-UHFFFAOYSA-N sodium silicate Chemical compound [Na+].[Na+].[O-][Si]([O-])=O NTHWMYGWWRZVTN-UHFFFAOYSA-N 0.000 claims description 3
- 238000002791 soaking Methods 0.000 abstract description 3
- 239000013078 crystal Substances 0.000 abstract description 2
- 230000000694 effects Effects 0.000 abstract description 2
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- 230000002349 favourable effect Effects 0.000 abstract 1
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- FAPWRFPIFSIZLT-UHFFFAOYSA-M Sodium chloride Chemical compound [Na+].[Cl-] FAPWRFPIFSIZLT-UHFFFAOYSA-M 0.000 description 12
- 230000000052 comparative effect Effects 0.000 description 11
- 230000010287 polarization Effects 0.000 description 8
- 238000005260 corrosion Methods 0.000 description 7
- 230000007797 corrosion Effects 0.000 description 7
- 239000000243 solution Substances 0.000 description 7
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 6
- 239000011780 sodium chloride Substances 0.000 description 6
- VZSRBBMJRBPUNF-UHFFFAOYSA-N 2-(2,3-dihydro-1H-inden-2-ylamino)-N-[3-oxo-3-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)propyl]pyrimidine-5-carboxamide Chemical compound C1C(CC2=CC=CC=C12)NC1=NC=C(C=N1)C(=O)NCCC(N1CC2=C(CC1)NN=N2)=O VZSRBBMJRBPUNF-UHFFFAOYSA-N 0.000 description 4
- 238000004372 laser cladding Methods 0.000 description 4
- 150000001247 metal acetylides Chemical class 0.000 description 4
- 239000010941 cobalt Substances 0.000 description 3
- 229910017052 cobalt Inorganic materials 0.000 description 3
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 3
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- INZDTEICWPZYJM-UHFFFAOYSA-N 1-(chloromethyl)-4-[4-(chloromethyl)phenyl]benzene Chemical compound C1=CC(CCl)=CC=C1C1=CC=C(CCl)C=C1 INZDTEICWPZYJM-UHFFFAOYSA-N 0.000 description 1
- HMUNWXXNJPVALC-UHFFFAOYSA-N 1-[4-[2-(2,3-dihydro-1H-inden-2-ylamino)pyrimidin-5-yl]piperazin-1-yl]-2-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)ethanone Chemical compound C1C(CC2=CC=CC=C12)NC1=NC=C(C=N1)N1CCN(CC1)C(CN1CC2=C(CC1)NN=N2)=O HMUNWXXNJPVALC-UHFFFAOYSA-N 0.000 description 1
- LDXJRKWFNNFDSA-UHFFFAOYSA-N 2-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)-1-[4-[2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidin-5-yl]piperazin-1-yl]ethanone Chemical compound C1CN(CC2=NNN=C21)CC(=O)N3CCN(CC3)C4=CN=C(N=C4)NCC5=CC(=CC=C5)OC(F)(F)F LDXJRKWFNNFDSA-UHFFFAOYSA-N 0.000 description 1
- YLZOPXRUQYQQID-UHFFFAOYSA-N 3-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)-1-[4-[2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidin-5-yl]piperazin-1-yl]propan-1-one Chemical compound N1N=NC=2CN(CCC=21)CCC(=O)N1CCN(CC1)C=1C=NC(=NC=1)NCC1=CC(=CC=C1)OC(F)(F)F YLZOPXRUQYQQID-UHFFFAOYSA-N 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
- C23C4/12—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge characterised by the method of spraying
- C23C4/134—Plasma spraying
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
- C23C4/04—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge characterised by the coating material
- C23C4/06—Metallic material
- C23C4/067—Metallic material containing free particles of non-metal elements, e.g. carbon, silicon, boron, phosphorus or arsenic
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- Chemical & Material Sciences (AREA)
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- Plasma & Fusion (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Coating By Spraying Or Casting (AREA)
Abstract
The invention discloses a low-cost high-performance Fe-based superfine crystal plasma cladding layer and a preparation method thereof, wherein the cladding layer is prepared on a base material by adopting a plasma cladding method, and the alloy powder comprises the following components: 32.0-35.5 wt.% of ferrovanadium powder, 5.8-6.5 wt.% of graphite powder and 58.0-62.2 wt.% of reduced iron powder, and in the cladding process, spraying cooling water on the back surface of a molten pool on a substrate for water cooling, wherein the water spraying position on the substrate is kept right opposite to the molten pool, and the water spraying position moves along with the movement of the position of a cladding head forming the molten pool. Compared with the mode of soaking the base material in water, the invention adopts the follow-up water spraying and forced cooling, which is favorable for greatly reducing the generation of a vapor film and can obviously improve the heat dissipation effect of the base material. The prepared cladding layer has higher hardness and low cost.
Description
Technical Field
The invention relates to the technical field of plasma cladding, in particular to a low-cost high-performance Fe-based superfine crystal plasma cladding layer and a preparation method thereof.
Background
The abrasion and the corrosion are used as main failure modes of materials, which causes huge resource waste and economic loss, and the surface modification technology provides a good solution for the problems, wherein the service performance of surface strengthening methods such as spraying, electroplating and the like is influenced because the bonding strength of a coating/plating layer and a matrix is not high or the coating/plating layer is too thin.
The cladding layer which is clad by laser or plasma is metallurgically bonded with the base material, and the repair efficiency is higher. However, the laser cladding complete equipment has higher price and larger one-time investment. The common cladding material comprises iron-based, nickel-based and cobalt-based materials, wherein the price of the nickel-based and cobalt-based materials is 5-10 times that of the iron-based materials, and the nickel-based and cobalt-based materials are expensive. The in-situ authigenic vanadium carbide reinforced Fe-based cladding layer has good wear resistance, thermal and physical parameters similar to those of a steel workpiece, and the stress of the cladding layer is smaller. Chinese patent publication No. CN111809178A discloses 'a highly corrosion-resistant submicron-nanocrystalline Fe-based laser cladding layer and a preparation method thereof' invented by inventors of Zhang Qinglu university of industry, and the like, and a submicron-nanocrystalline VC/Fe composite laser cladding layer is prepared, wherein the hardness of the cladding layer is 790HV 0.2 The corrosion resistance is about 20 times of that of the low-carbon steel base material, but the preparation process window of the cladding layer is narrow, the grain size of the initial alloy powder needs to be variable-grain-size powder, and the thickness of the cladding layer is about 0.4 mm. And has high requirements on equipment and higher preparation cost.
The plasma cladding technology has the characteristics of low cost and the like, and compared with laser cladding, the plasma cladding layer has unsatisfactory comprehensive performance due to the problems of large thermal deformation of a base material, overhigh dilution rate and the like in the conventional plasma cladding.
Disclosure of Invention
The technical problem to be solved by the invention is as follows: provides a low-cost high-performance Fe-based ultrafine grain plasma cladding layer and a preparation method thereof.
In order to solve the technical problems, the invention provides a preparation method of a low-cost high-performance Fe-based ultrafine-grained plasma cladding layer, which is characterized in that the cladding layer is prepared on a base material by adopting a plasma cladding method, and the alloy powder comprises the following components: 32.0-35.5 wt.% of ferrovanadium powder, 5.8-6.5 wt.% of graphite powder and 58.0-62.2 wt.% of reduced iron powder, wherein in the cladding process, the back surface of a molten pool on a substrate is subjected to water cooling by spraying cooling water, the water spraying position on the substrate is kept right opposite to the molten pool, and the water spraying position moves along with the movement of the position of a cladding head forming the molten pool.
Preferably, the temperature of the cooling water is 18 ℃, and the flow rate of the cooling water is 6.5-8.5L/min.
Preference is given toThe ferrovanadium powder adopts FeV 50 And the particle diameters of the vanadium iron powder, the graphite powder and the reduced iron powder are all 75-150 mu m.
Preferably, the alloy powder is mixed in a V-shaped powder mixer, and is preset on the surface of the base material through water glass serving as a binder, wherein the thickness of the base material is about 0.8-1.2 mm.
Preferably, among the plasma cladding parameters, the welding current is 100-130A, the cladding speed is 2.0-3.0 mm/s, the ionic gas flow is 3L/min, the protective gas flow is 10L/min, and both the ionic gas and the protective gas adopt argon.
The low-cost high-performance Fe-based ultrafine grain plasma cladding layer is prepared by any one of the preparation methods of the low-cost high-performance Fe-based ultrafine grain plasma cladding layer.
The invention has the beneficial effects that: the invention keeps the following water spraying and strong cooling of the back base material of the molten pool in the plasma cladding process, accelerates the solidification and cooling speed of the molten pool, reduces the dilution rate of the cladding layer, closely refines the microstructure, and obviously improves the hardness and the corrosion resistance of the Fe cladding layer. In the cladding process, the forced cooling is applied to the base material, so that cladding heat can be conducted out in time, heat accumulation is reduced, residual stress is reduced, the solidification-cooling speed of a molten pool is increased, and finally the structure is refined. Compared with the mode of soaking the base material in water, the generation of a steam film is favorably and greatly reduced by adopting the follow-up water spraying forced cooling, and the heat dissipation effect of the base material can be obviously improved. The prepared cladding layer has higher hardness and low cost.
Drawings
In fig. 1:
a is the macroscopic morphology of the cross section of the cladding layer obtained in the comparative example 1-1,
b is the macroscopic appearance of the cross section of the cladding layer obtained in example 1,
c is the optical microscopic morphology of the cladding layer obtained in comparative example 1-1,
d is the optical microscopic morphology of the cladding layer obtained in example 1,
e is the secondary electron morphology of the cladding layer obtained in comparative example 1-1;
f is the secondary electron morphology of the cladding layer obtained in example 1;
FIG. 2 is a cross-sectional microhardness distribution curve of a cladding layer a, b, g and a low carbon steel substrate;
FIG. 3 is a potentiodynamic polarization curve of the clad layers a, b, g and the low-carbon steel substrate in a 3.5 wt.% NaCl solution;
FIG. 4 is a cross-sectional microhardness distribution curve of the cladding layers c, d, h, low carbon steel substrate;
FIG. 5 is a zeta potential polarization curve of the clad layers c, d, h, low carbon steel substrate measured in a 3.5 wt.% NaCl solution;
FIG. 6 is a cross-sectional microhardness distribution curve of a cladding layer e, f, i, low carbon steel substrate;
FIG. 7 is a zeta potential polarization curve of the clad layer e, f, i, low carbon steel substrate measured in a 3.5 wt.% NaCl solution.
DETAILED DESCRIPTION OF EMBODIMENT (S) OF INVENTION
The following examples prepare cladding layers by using pre-powder on mild steel substrates. The Fe-based alloy powder comprises the following components: ferrovanadium powder, graphite and reduced iron powder. FeV 50 The particle size ranges of the three powders of the graphite and the reduced iron powder are 75-150 mu m. Firstly, mixing alloy powder in a V-shaped powder mixer, and then presetting the mixed alloy powder on the surface of a substrate by using water glass as a binder to obtain a preset layer, wherein the thickness of the preset layer is about 1.0 mm. The alloy powder is prepared according to the proportion in the table 1. FeV is adopted as ferrovanadium powder 50 。
TABLE 1
| Serial number | Ferrovanadium powder | Graphite | Reduced iron powder | Cladding layer |
| Comparative example 1-1 | 34.0wt.％ | 6.0wt.％ | 60.0wt.％ | a |
| Comparative examples 1 to 2 | 34.0wt.％ | 6.0wt.％ | 60.0wt.％ | g |
| Example 1 | 34.0wt.％ | 6.0wt.％ | 60.0wt.％ | b |
| Comparative example 2-1 | 32.0wt.％ | 5.8wt.％ | 62.2wt.％ | c |
| Comparative example 2-2 | 32.0wt.％ | 5.8wt.％ | 62.2wt.％ | h |
| Example 2 | 32.0wt.％ | 5.8wt.％ | 62.2wt.％ | d |
| Comparative example 3-1 | 35.5wt.％ | 6.5wt.％ | 58.0wt.％ | e |
| Comparative example 3-2 | 35.5wt.％ | 6.5wt.％ | 58.0wt.％ | i |
| Example 3 | 35.5wt.％ | 6.5wt.％ | 58.0wt.％ | f |
Comparative examples 1-1, 2-1 and 3-1 cladding conditions: plasma cladding parameters with air cooling of the substrate: welding current is 120A, cladding speed is 2.5mm/s, ion gas (argon) flow is 3L/min, and shielding gas (argon) flow is 10L/min, so that cladding layers a, c and e are prepared.
Comparative examples 1-2, 2-2, 3-2 cladding conditions: the substrate was completely immersed in cooling water, which was maintained at 18 ℃ by immersion water cooling. Plasma cladding parameters: welding current is 120A, cladding speed is 2.5mm/s, ion gas (argon) flow is 3L/min, shielding gas (argon) flow is 10L/min, and cladding layers g, h and i are prepared.
Examples 1, 2, 3 cladding conditions: plasma cladding parameters of the substrate cooled by water spray: welding current is 120A, cladding speed is 2.5mm/s, ion gas (argon) flow is 3L/min, shielding gas (argon) flow is 10L/min, water is sprayed to the substrate on the back of the molten pool to be cooled, cooling water temperature is 18 ℃, cooling water pump flow is 8L/min, the water spraying position on the substrate is kept opposite to the molten pool, and the water spraying position moves along with the movement of the position of a cladding head forming the molten pool, so that cladding layers b, d and f are prepared.
As can be seen from FIGS. 1a and b, the cross-sectional shape of the cladding layer of the air-cooled and water-cooled base material is changed from an oval shape to a flat shape, and the width-to-depth ratio of the cladding layer is increased.
Table 1 shows the penetration and the width of the cladding layer of the air-cooled and water-cooled base material and the width of the heat affected zone. Compared with an air-cooled base material cladding layer, the depth of the water-sprayed water-cooled base material cladding layer is reduced by about 48.38%, the width of the water-sprayed water-cooled base material cladding layer is reduced by about 27.78%, the heat affected zone is reduced by about 36.29%, and the dilution rate of the water-sprayed water-cooled base material cladding layer is reduced by 16.90%.
TABLE 2 penetration, Width of fusion and Width of Heat affected zone of air-and water-cooled cladding layers
| Cladding layer | Cladding Cooling Condition | Penetration/mm | Melt width/mm | Heat affected zone/mm |
| Cladding layer a | Air cooling | 1.24 | 5.40 | 1.75 |
| Cladding layer b | Water spraying and cooling | 0.64 | 3.90 | 1.12 |
| Cladding layer g | Immersion water cooling | 0.99 | 3.60 | 1.52 |
The average grain sizes of the cladding layer a and the cladding layer b obtained by the test are respectively 3.12 mu m and 1.39 mu m, and 42.6 percent of matrix grains in the cladding layer of the water-spraying water-cooling base material reach submicron scale. See the cladding layer optical microscopic morphology shown in fig. 1c, d.
As can be seen from FIGS. 1e and f, in the air-cooled and water-cooled base material cladding layer, carbides are aggregated and distributed along the grain boundary, the number of carbides in the water-cooled base material cladding layer is large, the size of the carbides is obviously reduced, and the average grain sizes of the carbides in the air-cooled and water-cooled base material cladding layer are respectively 0.37 μm and 0.09 μm.
As can be seen from fig. 2, 4 and 6, the hardness of the water-spray water-cooled base material cladding layer is higher than that of the water-cooled and air-cooled base material cladding layer. The average hardness of the cladding layers of the air-cooled, water-cooled and water-cooled base materials in the first group is 782HV 0.2 、896HV 0.2 、1040HV 0.2 The microhardness of the water spraying and water cooling base material cladding layer is improved by 258HV compared with that of the air cooling base material cladding layer 0.2 The microhardness of the water-spraying water-cooling base material cladding layer is improved by 144HV compared with the microhardness of the water-soaking water-cooling base material cladding layer 0.2 . The average hardness of the cladding layers of the air-cooled, water-cooled immersed and water-cooled base materials in the second group is 753HV 0.2 、879.3HV 0.2 And 1015HV 0.2 The microhardness of the water spraying water cooling base material cladding layer is improved by 262HV compared with the microhardness of the air cooling base material cladding layer 0.2 Microscopic of water-spraying and water-cooling base material cladding layerThe hardness is increased by 135.7HV compared with the microhardness of the cladding layer of the immersed water-cooled base material 0.2 . The average hardness of the air-cooled, water-cooled immersion and water-cooled substrate cladding layers in the third group is 801HV 0.2 、910.3HV 0.2 And 1061HV 0.2 The microhardness of the water spraying and water cooling base material cladding layer is improved by 260HV compared with that of the air cooling base material cladding layer 0.2 The microhardness of the water-spraying water-cooling base material cladding layer is improved by 150.7HV compared with the microhardness of the water-cooling base material cladding layer 0.2 。
FIG. 3 is a potentiodynamic polarization curve of the clad layers a, b, g and the low carbon steel substrate measured in a 3.5 wt.% NaCl solution. FIG. 5 is a potentiodynamic polarization curve of the clad layers c, d, h and the low carbon steel substrate measured in a 3.5 wt.% NaCl solution. FIG. 7 is a potentiodynamic polarization curve of the clad layers e, f, i and the low carbon steel substrate measured in a 3.5 wt.% NaCl solution. Table 3 shows the results of fitting the polarization curves in fig. 3, 5 and 7, and it can be seen from the fitting results that the corrosion resistance of the water-sprayed and water-cooled base material cladding layer in the first group is about 3.10 times that of the air-cooled base material cladding layer, about 2.50 times that of the water-sprayed and water-cooled base material cladding layer, and about 13.75 times that of the mild steel base material. The corrosion resistance of the water spraying and water cooling base material cladding layer in the second group is about 2.60 times that of the air cooling base material cladding layer, about 2.10 times that of the cladding layer immersed in the water cooling base material cladding layer and about 12.23 times that of the low carbon steel base material. The corrosion resistance of the water spraying and water cooling base material cladding layer in the third group is about 2.76 times of that of the air cooling base material cladding layer, about 2.04 times of that of the low carbon steel base material cladding layer which is immersed in the water cooling base material cladding layer and about 12.72 times of that of the low carbon steel base material.
TABLE 3 polarization curve fitting results of cladding and low carbon steel
The above description is only a preferred embodiment of the present invention and is not intended to limit the present invention, and various modifications and changes may be made by those skilled in the art. Any modification, equivalent replacement, or improvement made within the spirit and principle of the present invention should be included in the protection scope of the present invention.
Claims (6)
1. A preparation method of a low-cost high-performance Fe-based ultrafine grain plasma cladding layer is characterized by comprising the following steps: preparing a cladding layer on a base material by adopting a plasma cladding method, wherein the alloy powder comprises the following components: 32.0-35.5 wt.% of ferrovanadium powder, 5.8-6.5 wt.% of graphite powder and 58.0-62.2 wt.% of reduced iron powder, and in the cladding process, spraying cooling water on the back surface of a molten pool on a substrate for water cooling, wherein the water spraying position on the substrate is kept right opposite to the molten pool, and the water spraying position moves along with the movement of the position of a cladding head forming the molten pool.
2. The method for preparing the Fe-based ultrafine grained plasma cladding layer with low cost and high performance according to claim 1, characterized in that: the temperature of the cooling water is 18 ℃, and the flow rate of the cooling water is 6.5-8.5L/min.
3. The method of claim 1, wherein FeV is used as FeV powder for the preparation of the Fe-based ultrafine plasma cladding layer with low cost and high performance 50 And the particle diameters of the vanadium iron powder, the graphite powder and the reduced iron powder are all 75-150 mu m.
4. The method for preparing the Fe-based ultrafine grained plasma cladding layer with low cost and high performance according to claim 1, characterized in that: firstly, alloy powder is mixed in a V-shaped powder mixer, and is preset on the surface of a base material through water glass serving as a binder, wherein the thickness of the base material is about 0.8-1.2 mm.
5. The method for preparing the Fe-based ultrafine grained plasma cladding layer with low cost and high performance according to claim 1, characterized in that: in the plasma cladding parameters, the welding current is 100-130A, the cladding speed is 2.0-3.0 mm/s, the ionic gas flow is 3L/min, the protective gas flow is 10L/min, and argon is used for the ionic gas and the protective gas.
6. A low-cost high-performance Fe-based ultrafine grain plasma cladding layer is characterized in that: the Fe-based ultrafine grained plasma cladding layer prepared by the method of any one of claims 1 to 5 with low cost and high performance.
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN116695116A (en) * | 2023-07-03 | 2023-09-05 | 齐鲁工业大学(山东省科学院) | Submicron-nanometer Fe-based plasma cladding layer and preparation method thereof |
| CN116926538A (en) * | 2023-08-02 | 2023-10-24 | 齐鲁工业大学(山东省科学院) | Self-passivation high corrosion-resistant Fe-VC composite laser cladding layer and preparation method thereof |
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| CN116926538B (en) * | 2023-08-02 | 2024-03-12 | 齐鲁工业大学(山东省科学院) | Self-passivation high corrosion-resistant Fe-VC composite laser cladding layer and preparation method thereof |
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