CN116329571A - TiC reinforced FeCrNiMo gradient coating prepared by laser cladding - Google Patents

TiC reinforced FeCrNiMo gradient coating prepared by laser cladding Download PDF

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CN116329571A
CN116329571A CN202310324656.8A CN202310324656A CN116329571A CN 116329571 A CN116329571 A CN 116329571A CN 202310324656 A CN202310324656 A CN 202310324656A CN 116329571 A CN116329571 A CN 116329571A
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cladding
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fecrnimo
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贾娜
余本军
张纯朴
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Northeast Forestry University
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    • B—PERFORMING OPERATIONS; TRANSPORTING
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    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y70/00—Materials specially adapted for additive manufacturing
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    • C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
    • C22C29/06—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds
    • C22C29/067—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds comprising a particular metallic binder
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
    • C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
    • C22C29/06—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds
    • C22C29/10—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds based on titanium carbide
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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Abstract

The application belongs to the field of laser cladding, and particularly relates to a method for preparing a composite wear-resistant coating by laser cladding. The method comprises the steps of carrying out laser cladding on prefabricated alloy powder to obtain a cladding layer, wherein the prefabricated alloy powder is a mixture of FeCrNiMo and TiC, the cladding layer is five layers, the three front gradient cladding layers mainly comprise Fe, cr, fe-Cr and other element compounds, the four gradient cladding layers find (Cr, fe) 7C3, and the five gradient cladding layers have TiC (Cr, fe) 7C3 and TiC and play a role in dispersion strengthening. The TiC reinforced iron-based gradient coating with compact tissue and no defects is prepared by the method.

Description

TiC reinforced FeCrNiMo gradient coating prepared by laser cladding
Technical Field
The invention belongs to the technical field of laser cladding, relates to a method for preparing a TiC reinforced FeCrNiMo gradient coating by laser cladding, and further relates to a method for preparing the TiC reinforced FeCrNiMo gradient coating by laser cladding.
Background
Along with the rapid growth of social economy, the science and technology of China rapidly develops, and meanwhile, the production scale of mechanical parts of China is larger and larger. Therefore, the stability requirements of mechanical equipment and manufactured products are more strict, and in order to meet the requirements, parts with good performance, high strength and high reliability are required to be manufactured, and the parts are usually manufactured by forging, welding and the like, and the required size precision and shape are obtained by machining at a later stage. However, the parts operate in a severe environment for a long time, and many key parts are corroded, worn, broken and the like, so that the parts fail and cannot continue to operate stably, and the economic loss can be reduced by improving the performance of the parts. The surface of the reinforced part can effectively reduce part failure, increase the stability of the part and prolong the service life of the part, thereby reducing the cost of the mechanical part manufacturing industry and improving the economic benefit of China, and therefore, the surface reinforcement treatment of the part is imperative. In recent years, laser cladding remanufacturing has very wide application, and in particular, several typical industries have wide market scale, such as large mining machinery, petrochemical industry, electric power, railway, automobile, navigation, metallurgy, aviation, mold and other industries. From the research conditions at home and abroad at present, the research on improving the performance of the Fe-based coating by laser cladding TiC ceramic particles in recent years is mainly focused on the basic theory of cladding, the technological parameters of cladding layer preparation, the performance test of a single-channel cladding layer and the like, and because the physical and chemical properties between the Fe-based alloy and TiC hard phase are too large, the problems of stress concentration, cracks, easy falling of the coating and the like easily occur, and the adoption of the laser cladding to prepare the gradient coating can effectively reduce the stress between TiC of the Fe-based alloy and reduce the problems, so that the research on the preparation of the TiC gradient coating by laser cladding has important significance.
Disclosure of Invention
The invention aims to provide a preparation method for preparing TiC reinforced FeCrNiMo gradient coating based on laser cladding.
The invention is realized by the following technical scheme:
preparing FeCrNiMo-based gradient coatings with different TiC contents on 42CrMo by adopting a laser cladding technology, and aiming at improving the hardness and the wear resistance of a matrix; preparing a TiC gradient coating with compact tissue and no defects by regulating and controlling the proportion of the coating materials and optimizing cladding process parameters; the method is implemented according to the following steps:
step 1: powder preparation, wherein the coating in the experiment mainly comprises FeCrNiMo-based alloy powder and TiC powder, and the two powders are placed in a drying oven for 12 hours, and the temperature is set at 80 ℃ so as to remove water vapor in the powder;
step 2: preparing a sample matrix, processing a 42CrMo steel matrix into a size of 100 multiplied by 10mm by adopting a wire-cut electric discharge machine, polishing the surface of the matrix by using a grinding wheel and sand paper to remove a surface oxide layer, and cleaning surface impurities and greasy dirt by using alcohol and acetone;
step 3: powder feeder parameter setting, the mixing of powder adopts the coaxial powder that send of twin-tub, guarantees powder misce bene and is convenient for control powder content. Powder feeding speed is 20g/min in the cladding process, and argon flow speed is controlled at 15L/min;
step 4: setting laser parameters, namely setting the laser power to be 600W-2200W and the scanning speed to be 4.6-5.4m/s;
step 5: starting single-pass laser cladding on the surface of a 42CrMo steel matrix, carrying out multiple experiments, and selecting technological parameters;
step 6: and (3) starting to perform gradient multilayer multi-channel laser cladding of different types on the surface of the 42CrMo steel matrix.
In step (1), the content of each element of the FeCrNiMo-based alloy powder is c0.14wt.%, mo1.04wt.%, ni1.47wt.%, cr15.04wt.%, si0.97wt.%, b1.29wt.% and the balance iron (Fe).
In the step (3), the coating mixed powder mainly consists of FeCrNiMo-based alloy powder and TiC powder; the FeCrNiMo alloy powder is mixed according to the proportion of 50-90% of the total mass of the mixed powder, and the balance is TiC powder; the powder feeder adopts 99.99% argon as protective gas.
In the step (5), single-pass laser cladding is started on the surface of a 42CrMo steel matrix, and through multiple experiments, the technological parameters of laser power 1200W, scanning speed 5mm/s, powder feeding speed 20g/min and defocusing amount 0mm are finally selected, wherein 99.99% argon is adopted for protection in the cladding process, and the argon flow rate is controlled at 15L/min; the mixing of the powder adopts double-barrel coaxial powder feeding, which ensures the uniformity of powder mixing and is convenient for controlling the powder content.
In the step (6), the surface of the 42CrMo steel matrix is subjected to multi-layer multi-coating laser cladding into 5 groups, tiC iron-based alloy powder of the coating is subjected to powder mixing according to a gradient of 10% of each total mass of mixed powder, the TiC iron-based alloy powder of each layer is increased by 10%, and the balance is FeCrNiMo powder.
According to the technical scheme, compared with the prior art, the invention has the following effects.
The TiC reinforced FeCrNiMo gradient composite coating is successfully prepared by adopting a Selective Laser Melting (SLM) additive manufacturing process; the three-layer gradient cladding layer mainly comprises Fe, cr, fe-Cr and other element compounds, four-layer gradient cladding layers find that (Cr, fe) 7C3 and five-layer gradient cladding layers have TiC, and the (Cr, fe) 7C3 and TiC play a role in dispersion strengthening, so that the mechanical property of the cladding layers is enhanced.
As the TiC content increases, the gradient coating hardness increases and the fifth layer hardness reaches 779HV0.2 at maximum.
The wear resistance of the gradient coating gradually increases along with the increase of the TiC content; one layer and two layers of wear mechanisms are abrasive wear, three to five layers of wear mechanisms are abrasive wear and adhesive wear, and the wear amounts of one to five layers are 0.8mg, 0.62mg, 0.55mg, 0.31mg and 0.2mg respectively; the abrasion loss gradually decreases as the TiC content of the coating gradient increases.
Drawings
FIG. 1 is a graph showing the macroscopic morphology of samples of TiC-enhanced FeCrNiMo gradient coatings to be prepared by laser cladding in examples 1, 2, 3, 4 and 5 of the present invention.
FIG. 2 is an X-ray diffraction pattern of different TiC-enhanced FeCrNiMo gradient coatings prepared in examples 1, 2, 3, 4, 5 of the present invention.
FIG. 3 is a microstructure of different TiC-enhanced FeCrNiMo gradient coatings prepared in examples 1, 2, 3, 4, 5 of the present invention.
FIG. 4 shows the microhardness of different TiC-enhanced FeCrNiMo gradient coatings prepared in examples 1, 2, 3, 4 and 5 of the present invention.
FIG. 5 shows the wear values of different TiC-enhanced FeCrNiMo gradient coatings prepared in examples 1, 2, 3, 4 and 5 of the present invention.
FIG. 6 is a graph showing the friction coefficient of different TiC-enhanced FeCrNiMo gradient coatings prepared in examples 1, 2, 3, 4 and 5 of the present invention.
Detailed Description
Example 1
Step 1, preparing powder: the coating in the experiment mainly comprises FeCrNiMo-based alloy powder and TiC powder, and the two powders are placed in a drying oven for 12 hours, and the temperature is set at 80 ℃ so as to remove water vapor in the powder;
step 2, preparing a sample matrix, namely processing a 42CrMo steel matrix into a size of 100 multiplied by 10mm by adopting a wire cut electric discharge machine, polishing the surface of the matrix by using a grinding wheel and sand paper to remove a surface oxide layer, and cleaning surface impurities and greasy dirt by using alcohol and acetone;
step 3, setting parameters of the powder feeder: the mixing of the powder adopts double-barrel coaxial powder feeding, which ensures the uniformity of powder mixing and is convenient for controlling the powder content. Powder feeding speed is 20g/min in the cladding process, and argon flow speed is controlled at 15L/min;
step 4, setting laser parameters: the laser power is 600W-2200W, and the scanning speed is 4.6-5.4m/s;
step 5, starting single-pass laser cladding on the surface of the 42CrMo steel matrix, carrying out multiple experiments, and selecting technological parameters;
and 6, starting to carry out laser cladding of a plurality of layers of coating layers on the surface of the 42CrMo steel substrate.
In step (1), the content of each element of the FeCrNiMo-based alloy powder is c0.14wt.%, mo1.04wt.%, ni1.47wt.%, cr15.04wt.%, si0.97wt.%, b1.29wt.% and the balance iron (Fe).
The particle size of the iron-based powder is 53-150 mu m, the particle size of TiC ceramic particles is 45-75 mu m, the specification difference of the particle sizes of the iron-based powder and the TiC ceramic particles is smaller, and the quality of the coating can be ensured.
In the step (3), coating mixed powder for the second experiment mainly consists of FeCrNiMo-based alloy powder and TiC powder; the FeCrNiMo-based alloy powder is mixed according to the proportion of 50-90% of the total mass of the mixed powder, and the balance is TiC powder; the powder feeder adopts 99.99% argon as protective gas.
In the step (5), single-pass laser cladding is started on the surface of the 42CrMo steel matrix, and through multiple experiments, the technological parameters of laser power 1200W, scanning speed 5mm/s, powder feeding speed 20g/min and defocusing amount 0mm are finally selected, wherein 99.99% argon is adopted for protection in the cladding process, and the argon flow rate is controlled at 15L/min. The mixing of the powder adopts double-barrel coaxial powder feeding, which ensures the uniformity of powder mixing and is convenient for controlling the powder content.
In the step (6), the surface of the 42CrMo steel matrix is subjected to single-layer multi-layer coating laser cladding, wherein TiC iron-based alloy powder of the coating is 10% of the total mass of the mixed powder, and FeCrNiMo powder is 90% of the total mass.
Example 2
The difference between this example and example 1 is that the laser cladding of the two layers of the multi-layer coating layer is started on the surface of the 42CrMo steel substrate in the step (6), the first layer coating layer is the same as that in example 1, and the cladding of the second layer coating layer is started on the basis of the first layer coating layer, the TiC powder of the second layer coating layer is 20% of the total mass of the mixed powder, and the FeCrNiMo powder is 80% of the total mass of the mixed powder.
Example 3
The difference between this example and example 2 is that the laser cladding of the three layers of multi-layer coating layer is started on the surface of the 42CrMo steel substrate in the step (6), the first two layers of coating layers are the same as in example 2, and the cladding of the third layer of coating layer is started on the basis of the second layer of coating layer, wherein the TiC powder of the third layer of coating layer is 30% of the total mass of the mixed powder, and the FeCrNiMo is 70% of the total mass of the mixed powder.
Example 4
The difference between this example and example 3 is that the laser cladding of the two layers of the multi-layer coating layer is started on the surface of the 42CrMo steel substrate in the step (6), the steps of the first three layers of the coating layer are the same as those in example 3, and the cladding of the fourth layer of the coating layer is started on the basis of the third layer of the coating layer, the TiC powder of the fourth layer of the coating layer is 40% of the total mass of the mixed powder, and the FeCrNiMo powder is 60% of the total mass of the mixed powder.
Example 5
This example differs from example 4 in that the five-layer multi-layer coating laser cladding is started on the surface of the 42CrMo steel substrate as described in step (6), the first four layer coating steps are the same as in example 4, and the cladding of the fifth layer coating is started on the basis of the fourth layer coating, the TiC powder of the fifth layer coating is 50% of the total mass of the mixed powder, and the FeCrNiMo powder is 50% of the total mass.
And preparing TiC reinforced FeCrNiMo gradient coating interfaces and characterizing mechanical properties by laser cladding.
The samples 1, 2, 3, 4 and 5 are prepared in the embodiment, the phase composition of the samples is detected by an X-ray diffractometer (XRD), the cross section morphology of a cladding layer is mainly observed and the tissue characteristics are analyzed by a metallographic microscope scanning electron microscope, the hardness of a coating is measured by a Vickers hardness tester, the frictional wear performance is measured by a high-temperature vacuum pin plate frictional wear testing machine in a wear test manner, the morphology of SEM abrasion marks is observed by a scanning electron microscope, and the wear mechanism is analyzed; the measurement results are shown in FIGS. 1-5, and the measurement result surfaces are shown.
In fig. 1: (a) A TiC powder cladding layer sample with the content of 10% is clad; (b) Cladding TiC powder with the first layer content of 10% and cladding TiC powder cladding layer sample with the second layer content of 20%; (c) Cladding TiC powder with the content of 10% of the first layer, cladding TiC powder with the content of 20% of the second layer and cladding TiC powder cladding layer sample with the content of 30% of the third layer; (d) For cladding TiC powder with the first layer content of 10%, cladding TiC powder with the second layer content of 20%, cladding TiC powder with the third layer content of 30%, cladding TiC powder cladding layer sample with the fourth layer content of 40%; (e) For cladding TiC powder with 10% of the first layer, tiC powder with 20% of the second layer, tiC powder with 30% of the third layer, tiC powder with 40% of the fourth layer and TiC powder cladding layer sample with 50% of the fifth layer.
Through the graph2, examples 1, 2, 3, 4, 5, the XRD patterns of different TiC content gradient coatings were analyzed, and according to the phase results analysis, it was shown that: the main phase composition of the single-layer double-layer and three-layer gradient cladding layer is an element compound of Fe, cr, fe-Cr and the like, when the TiC content is low, the cladding layer is less in derivative, and four layers of gradient cladding layers are formed (Cr, fe) 7 C 3 TiC, (Cr, fe) appears on the five-layer gradient cladding layer 7 C 3 And TiC plays a role in dispersion strengthening, so that the mechanical property of the cladding layer is improved.
Through fig. 3, examples 1, 2, 3, 4 and 5, the gradient coating prepared by laser cladding has good metallurgical bonding among different cladding layers, the cladding layers mainly comprise cellular tissues and dendritic tissues, the cellular tissues and dendritic tissues of the fifth cladding layer are refined again, a large number of black TiC particles appear, and the performance is remarkably improved.
With examples 1, 2, 3, 4, 5 in fig. 4, the hardness of the coating layer tends to increase in gradient with increasing TiC content, and the hardness of the fifth layer reaches 779HV0.2 at maximum.
In fig. 5 to 6, in examples 1, 2, 3, 4 and 5, the abrasion loss of the base material was very large, the abrasion loss gradually decreased as the TiC content of the coating gradient was increased, the abrasion loss reached minimum at the fifth layer gradient, and the three layers of 10% TiC-30% TiC cladding layers had very stable and minimum friction coefficients, and the abrasion resistance of the coating increased as the TiC content was increased.

Claims (8)

1. A preparation method for preparing TiC reinforced FeCrNiMo gradient coating based on laser cladding is characterized in that FeCrNiMo gradient coatings with different TiC contents are prepared on 42CrMo by adopting a laser cladding technology; the TiC gradient coating with compact tissue and no defects is prepared by regulating and controlling the proportion of the coating materials and optimizing the cladding process parameters.
2. The preparation method for preparing the TiC reinforced FeCrNiMo gradient coating based on the laser cladding according to claim 1, wherein the FeCrNiMo gradient coating with different TiC contents has five layers, the three previous gradient cladding layers mainly comprise Fe, cr, fe-Cr and other element compounds, the four gradient cladding layers find (Cr, fe) 7C3, and the five gradient cladding layers have TiC.
3. A method of selective laser melting an in situ WC ceramic matrix composite prepared according to claim 1 comprising the steps of:
(1) Preparing mixed powder
Placing FeCrNiMo-based alloy powder and TiC powder into a drying oven for 12h, and setting the temperature to 80 ℃ to remove water vapor in the powder;
(2) Sample matrix preparation
Machining a 42CrMo steel matrix into a size of 100 multiplied by 10mm by adopting a wire cut electric discharge machine, polishing the surface of the matrix by using a grinding wheel and sand paper to remove a surface oxide layer, and cleaning surface impurities and greasy dirt by using alcohol and acetone;
(3) Powder feeder parameter setting
The mixing of the powder adopts double-barrel coaxial powder feeding, which ensures the uniformity of powder mixing and is convenient for controlling the powder content. Powder feeding speed is 20g/min in the cladding process, and argon flow speed is controlled at 15L/min;
(4) Laser parameter setting
The laser power is 600W-2200W, and the scanning speed is 4.6-5.4m/s;
(5) Technological parameter selection and laser cladding
Starting single-pass laser cladding on the surface of a 42CrMo steel matrix, carrying out multiple experiments, and selecting technological parameters; and (3) starting to carry out laser cladding of different types of gradient multilayer multi-layer coating layers on the surface of the 42CrMo steel substrate.
4. A method of selective area laser melting of an in situ WC ceramic based composite prepared according to claim 3 wherein the FeCrNiMo based alloy powder in step (1) has an element content of c0.14wt.%, mo1.04wt.%, ni1.47wt.%, cr15.04wt.%, si0.97wt.%, b1.29wt.% with the remainder being iron (Fe).
5. The method for preparing an in-situ WC ceramic-based composite material by selective laser melting according to claim 4, wherein the particle size of the iron-based powder is 53-150 μm, and the particle size of the TiC ceramic particles is 45-75 μm.
6. A method of selective laser melting prepared in situ WC ceramic matrix composite according to claim 3, wherein in step (3), the coating mixed powder is mainly composed of FeCrNiMo base alloy powder and TiC powder; the FeCrNiMo alloy powder is mixed according to the proportion of 50-90% of the total mass of the mixed powder, and the balance is TiC powder.
7. The method for preparing the in-situ WC ceramic matrix composite material by selective laser melting according to claim 3, wherein in the step (5), single-pass laser cladding is started on the surface of a 42CrMo steel matrix, and through multiple experiments, the technological parameters of 1200W of laser power, 5mm/s of scanning speed, 20g/min of powder feeding speed and 0mm of defocusing amount are finally selected, wherein 99.99% of argon is adopted for protection in the cladding process, and the argon flow rate is controlled at 15L/min; the mixing of the powder adopts double-barrel coaxial powder feeding, which ensures the uniformity of powder mixing and is convenient for controlling the powder content.
8. The method for preparing an in-situ WC ceramic matrix composite material by selective laser melting according to claim 3, wherein in the step (6), the surface of the 42CrMo steel matrix is subjected to multi-layer multi-coating laser cladding and divided into 5 groups, tiC iron-based alloy powder of the coating is subjected to powder preparation according to a gradient of 10% of the total mass of the mixed powder, the TiC iron-based alloy powder of each layer is increased by 10%, and the balance is FeCrNiMo powder.
CN202310324656.8A 2023-03-30 2023-03-30 TiC reinforced FeCrNiMo gradient coating prepared by laser cladding Pending CN116329571A (en)

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