Method for manufacturing nickel-based superalloy by regulating and controlling laser additive material through portable ultrasonic impact equipment

Abstract

The invention discloses a method for manufacturing nickel-based superalloy by regulating and controlling laser additive materials through portable ultrasonic impact equipment, a nickel-based superalloy structure is obtained on a substrate according to the following steps on the substrate for at least one time, and the step comprises the steps that nickel-based superalloy powder is subjected to N times of laser melting deposition on the substrate to form N deposition layers, wherein N is equal to 1-10; and performing primary ultrasonic peening on the deposition layer on the substrate. The microhardness of the nickel-based superalloy prepared through the method is remarkably improved, the improvement rate ranges from 15% to 40%, and the method has the advantages of being convenient to use, low in cost, rapid in forming, easy to operate, capable of conducting machining treatment according to requirements, wide in application range and the like.

Description

Technical Field

[0001] The present invention belongs to the technical field of laser additive manufacturing, and specifically relates to a method for manufacturing nickel-based high-temperature alloys by controlling laser additive manufacturing using a portable ultrasonic impact device. Background Art

[0002] Nickel-based superalloys have high tensile and yield strength, excellent ductility, good fatigue durability, and good creep resistance at high temperatures, making them widely used in the aerospace field. Additive manufacturing technology provides a new manufacturing method for complex structural metal components, with the characteristics of low cost, no molds required, and rapid manufacturing. It is an extremely excellent forming and manufacturing method for nickel-based superalloys that are prone to component segregation. At present, nickel-based superalloys have been widely used in the research and development and preparation of related products through additive manufacturing technology.

[0003] Among them, laser additive manufacturing has the characteristics of low cost, no need for molds and rapid manufacturing. However, due to the complexity of rapid prototyping and unstable laser parameters in remanufacturing projects, it is easy to cause problems such as poor quality of laser additively formed parts, coarse microstructure and mechanical properties that are difficult to meet the application requirements of high-end components, which seriously affect the use of parts. Summary of the invention

[0004] In view of the shortcomings of the prior art, the purpose of the present invention is to provide a method for manufacturing nickel-based high-temperature alloys by controlling laser additive manufacturing using a portable ultrasonic impact device. The method effectively combines laser additive manufacturing technology with convenient ultrasonic impact technology, uses laser melting deposition for laser additive manufacturing, and applies different frequencies between laser melting deposition and ultrasonic impact. The nickel-based high-temperature alloy can be regulated during the manufacturing process to achieve more precise organizational control and performance optimization.

[0005] The purpose of the present invention is achieved through the following technical solutions.

[0006] A method for regulating laser additive manufacturing of nickel-based high-temperature alloy structure, performing the following steps on a substrate at least once to obtain a nickel-based high-temperature alloy structure on the substrate, the steps comprising:

[0007] Step 1, performing N laser melting deposition on a substrate to form N deposition layers, wherein N=1-10, the laser power of the laser melting deposition is 500-3000W, the scanning speed of the laser melting deposition is 1-15mm / s, and the powder feeding rate of the laser melting deposition is 5-50g / min;

[0008] In step 1, the substrate is a 304 stainless steel plate, and the nickel-based high-temperature alloy powder is a spherical powder of GH4169 nickel-based high-temperature alloy.

[0009] In the step 1, the particle size of the nickel-based high-temperature alloy powder is 53 to 150 μm.

[0010] In step 1, the substrate is derusted before laser melting deposition.

[0011] In step 1, the powder feeder is operated for 15 to 20 seconds before laser melting deposition.

[0012] In the step 1, the gas atmosphere of the laser melting deposition is an inert gas or nitrogen.

[0013] In the above technical solution, the inert gas is argon.

[0014] Step 2, subjecting the deposited layer on the substrate to one ultrasonic impact, wherein the current intensity of the ultrasonic impact is 0.5-1.5A, the frequency of the ultrasonic impact is 10-20KHz, and the impact amplitude of the ultrasonic impact is 10-25μm.

[0015] The beneficial effects of the present invention are:

[0016] (1) The method of the present invention uses the laser process of laser melting deposition and ultrasonic impact to significantly improve the microhardness of the nickel-based high-temperature alloy structure, with an improvement rate ranging from 15% to 40%.

[0017] (2) The method of the present invention applies different frequencies between laser melting deposition and ultrasonic impact, so that after ultrasonic impact, the grain size of the nickel-based high-temperature alloy structure is significantly smaller than the grain size without ultrasonic impact. Before ultrasonic impact, the nickel-based high-temperature alloy structure prepared in Example 5 (i.e., the nickel-based high-temperature alloy prepared in Comparative Example 4) has an average particle size of 4.60 μm. After ultrasonic impact, the particle size is significantly reduced, and the average particle size is 2.75 μm.

[0018] (3) The method of the present invention has the characteristics of convenient use, low cost, rapid molding, simple operation, processing according to needs and wide application range. BRIEF DESCRIPTION OF THE DRAWINGS

[0019] Figure 1 (a) is the scanning electron microscopy structure of the nickel-based high-temperature alloy prepared in Comparative Example 4, Figure 1 (b) is the scanning electron microscopy structure of the nickel-based high-temperature alloy prepared in Example 5, Figure 1 (c) is the average grain size of the nickel-based high-temperature alloy structure prepared in Comparative Example 4, Figure 1 (d) is the average grain size of the nickel-based high-temperature alloy structure prepared in Example 5;

[0020] Figure 2 A comparison chart of the tensile properties of the nickel-based high-temperature alloy structures prepared in Examples 1 to 3 and Comparative Example 2;

[0021] Figure 3 This is a comparison chart of the microhardness of the nickel-based high-temperature alloy structures prepared in Examples 1 to 3 and Comparative Example 2.

[0022] Figure 4 It is a comparison chart of the microhardness of the nickel-based high-temperature alloy structures prepared in Examples 4 to 12 and Comparative Examples 3 to 11. DETAILED DESCRIPTION

[0023] The technical solution of the present invention is further described below in conjunction with specific embodiments.

[0024] In the following embodiments, the substrate is a 304 stainless steel substrate, and the nickel-based high-temperature alloy powder is a GH4169 nickel-based high-temperature alloy spherical powder.

[0025] Examples 1 to 12

[0026] A method for regulating laser additive manufacturing of nickel-based high-temperature alloy structure, wherein the substrate is derusted with an angle grinder, and then the substrate is wiped with anhydrous ethanol to remove oil stains, the substrate after degreasing is fixed on a workbench, nickel-based high-temperature alloy powder with a particle size of 53 to 150 μm is placed in a powder feeder, and the powder is operated for 15 seconds to ensure uniform powder feeding, and the following steps are performed M times on the substrate to obtain a nickel-based high-temperature alloy structure on the substrate, and the steps include:

[0027] Step 1, in an argon gas atmosphere, laser melting and depositing the nickel-based high-temperature alloy powder in the powder feeder on the substrate N times to form N deposition layers, wherein the laser power of the laser melting and deposition is G, the scanning speed of the laser melting and deposition is S, and the powder feeding rate of the laser melting and deposition is V;

[0028] Step 2: Use a portable ultrasonic impact device (model: UIT-125) to perform ultrasonic impact once on the deposited layer on the substrate, wherein the current intensity of the ultrasonic impact is 1A, the working frequency of the ultrasonic impact is 17.6KHz, and the impact amplitude of the ultrasonic impact is 12μm.

[0029] The N, M, G, S and V of the nickel-based high-temperature alloy structures prepared in Examples 1 to 12 are shown in Table 1.

[0030] Table 1

[0031] Example N M G S V Example 1 1 24 1000W 6mm / s 20g / min Example 2 3 8 1000W 6mm / s 20g / min Example 3 6 4 1000W 6mm / s 20g / min Example 4 1 1 1000W 4mm / s 15g / min Example 5 1 1 1000W 6mm / s 20g / min Example 6 1 1 1000W 8mm / s 10g / min Example 7 1 1 1400W 6mm / s 10g / min Example 8 1 1 1400W 4mm / s 15g / min Example 9 1 1 1400W 8mm / s 20g / min Example 10 1 1 1800W 8mm / s 20g / min Embodiment 11 1 1 1800W 6mm / s 15g / min Example 12 1 1 1800W 4mm / s 10g / min

[0032] Comparative Example 1

[0033] A method for regulating laser additive manufacturing of a high-temperature alloy is basically the same as Example 1, except that the nickel-based high-temperature alloy powder with a particle size of 53 to 150 μm is replaced by a stainless steel powder with a particle size of 53 to 150 μm.

[0034] Comparative Example 2

[0035] A method for manufacturing a nickel-based high-temperature alloy structure comprises: removing rust from a substrate by using an angle grinder, wiping the substrate with anhydrous ethanol to remove oil stains, placing the substrate after degreasing on a workbench, placing nickel-based high-temperature alloy powder with a particle size of 53 to 150 μm in a powder feeder, running for 15 seconds to ensure uniform powder feeding, and performing the following operations 24 times on the substrate to obtain a nickel-based high-temperature alloy structure on the substrate. The steps include: performing laser melting deposition on the nickel-based high-temperature alloy powder in the powder feeder on the substrate once in an argon gas atmosphere to form a deposition layer, wherein the laser power of the laser melting deposition is 1000 W, the scanning speed of the laser melting deposition is 6 mm / s, and the powder feeding rate of the laser melting deposition is 20 g / min.

[0036] Comparative Examples 3 to 11

[0037] A method for manufacturing a nickel-based high-temperature alloy structure is basically the same as that of comparative example 2, except that: in this comparative example, the steps are performed once on a substrate to obtain a nickel-based high-temperature alloy structure on the substrate. The laser power of the laser melting deposition is G, the scanning speed of the laser melting deposition is S, and the powder feeding rate of the laser melting deposition is V.

[0038] The G, S and V of the nickel-based high-temperature alloy structures prepared in Comparative Examples 3 to 11 are shown in Table 2.

[0039] Table 2

[0040] Comparative Example G S V Comparative Example 3 1000W 4mm / s 15g / min Comparative Example 4 1000W 6mm / s 20g / min Comparative Example 5 1000W 8mm / s 10g / min Comparative Example 6 1400W 6mm / s 10g / min Comparative Example 7 1400W 4mm / s 15g / min Comparative Example 8 1400W 8mm / s 20g / min Comparative Example 9 1800W 8mm / s 20g / min Comparative Example 10 1800W 6mm / s 15g / min Comparative Example 11 1800W 4mm / s 10g / min

[0041] Figure 1 (a) is the scanning electron microscopy structure of the nickel-based high-temperature alloy prepared in Comparative Example 4, Figure 1 (b) is the scanning electron microscopy structure of the nickel-based high-temperature alloy prepared in Example 5, Figure 1 (c) is the average grain size of the nickel-based high-temperature alloy structure prepared in Comparative Example 4, Figure 1 (d) is the average grain size of the nickel-based high-temperature alloy structure prepared in Example 5. Figure 1 (a) and (b) are used to calculate the average grain size of the nickel-based high-temperature alloy structure, such as Figure 1 As shown in (d) and (c), the average grain size of the nickel-based high-temperature alloy structure prepared in Comparative Example 4 is 4.60 μm; after ultrasonic impact (i.e., the nickel-based high-temperature alloy structure prepared in Example 5), its grain size is significantly reduced, and the average grain size is 2.75 μm. This further illustrates that after ultrasonic impact, the nickel-based high-temperature alloy structure prepared in Example 5 is subjected to plastic deformation, its grains are broken and refined, the grain size is significantly reduced, and the performance is improved.

[0042] Figure 2 The tensile properties of the nickel-based high-temperature alloys prepared in Examples 1 to 3 and Comparative Example 2 are compared. Figure 2 It can be seen that the average tensile strength of the nickel-based high-temperature alloy structure prepared in Comparative Example 2 is 888.10 MPa, the average tensile strength of the nickel-based high-temperature alloy structure prepared in Example 1 is 924.64 MPa, the average tensile strength of the nickel-based high-temperature alloy structure prepared in Example 2 is 910.83 MPa, and the average tensile strength of the nickel-based high-temperature alloy structure prepared in Example 3 is 917.99 MPa, and the tensile strength is significantly improved.

[0043] Figure 3 The microhardness comparison diagram of the nickel-based high-temperature alloy prepared in Examples 1 to 3 and Comparative Example 2 is shown in FIG. Figure 3 It can be seen that the average microhardness of the nickel-based high-temperature alloy prepared in Comparative Example 2 is 294.30 HV 0.2 The average microhardness of the nickel-based high-temperature alloy prepared in Example 1 is 323.02 HV 0.2 The average microhardness of the nickel-based high-temperature alloy prepared in Example 2 is 321.87 HV 0.2 The average microhardness of the nickel-based high-temperature alloy prepared in Example 3 is 319.57 HV 0.2 .

[0044] Figure 4 The microhardness comparison diagram of the nickel-based high-temperature alloys prepared in Examples 4 to 12 and Comparative Examples 3 to 11 is shown in FIG. Figure 4 It can be seen that the microhardness of the nickel-based high-temperature alloy tissues prepared by different laser processes after ultrasonic impact is significantly improved, and the improvement rate is in the range of 15% to 40%. Among them, the nickel-based high-temperature alloy tissue prepared in Comparative Example 11 (i.e., the nickel-based high-temperature alloy tissue prepared in Example 12) has the highest improvement rate of microhardness after ultrasonic impact, reaching 40%.

[0045] The method of the present invention can obtain nickel-based high-temperature alloy parts containing equiaxed crystals and columnar crystals as the microstructure. In addition, the method of the present invention can also be applied to laser additive manufacturing of other materials and can be applied to outdoor welding to regulate the structure and performance of different welding materials.

[0046] The present invention is described above by way of example. It should be noted that, without departing from the core of the present invention, any simple deformation, modification or other equivalent replacement that can be made by those skilled in the art without inventive effort falls within the protection scope of the present invention.

Claims

1. A method for regulating laser additive manufacturing of nickel-based high-temperature alloy structure, characterized in that: The following steps are performed at least once on the substrate to obtain a nickel-based high-temperature alloy structure on the substrate, the steps comprising: Step 1, performing N laser melting deposition on a substrate to form N deposition layers, wherein N=1-10, the laser power of the laser melting deposition is 500-3000W, the scanning speed of the laser melting deposition is 1-15mm / s, and the powder feeding rate of the laser melting deposition is 5-50g / min; Step 2, subjecting the deposited layer on the substrate to one ultrasonic impact, wherein the current intensity of the ultrasonic impact is 0.5-1.5A, the frequency of the ultrasonic impact is 10-20KHz, and the impact amplitude of the ultrasonic impact is 10-25μm.

2. The method according to claim 1, characterized in that The substrate is a 304 stainless steel plate, and the nickel-based high-temperature alloy powder is a GH4169 nickel-based high-temperature alloy spherical powder.

3. The method according to claim 1, characterized in that The particle size of the nickel-based high-temperature alloy powder is 53-150 μm.

4. The method according to claim 1, characterized in that The substrate was derusted before laser melting deposition.

5. The method according to claim 1, characterized in that The powder feeder was operated for 15 to 20 seconds before laser melting deposition.

6. The method according to claim 1, characterized in that The gas atmosphere of the laser melting deposition is an inert gas or nitrogen.

7. The method according to claim 6, characterized in that The inert gas is argon.

8. Use of the method as claimed in claim 1 in improving the tensile strength of nickel-based alloys.

9. Use of the method as claimed in claim 1 in improving the microhardness of nickel-based alloys.

10. Use of the method as claimed in claim 1 to reduce the average grain size of nickel-based alloy grains.

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