High-strength hydrogen embrittlement-resistant nickel-based high-temperature alloy and preparation process thereof

Abstract

The invention belongs to the technical field of metal material additive manufacturing, and particularly relates to a laser powder bed melting high-strength hydrogen embrittlement-resistant nickel-based superalloy and a preparation process thereof. By designing and optimizing a heat treatment process system, two-step solid solution and two-stage aging treatment are included, high-density fine strengthening phases and twin crystals are separated out in crystals, and the high-strength hydrogen embrittlement-resistant nickel-based superalloy is obtained; and low-index grains and a grain boundary short rod delta phase are formed through recrystallization, the strength and the hydrogen embrittlement resistance of the nickel-based alloy are synergistically improved, the tensile strength of the prepared nickel-based alloy is larger than or equal to 1300 MPa, the hydrogen embrittlement sensitivity is smaller than or equal to 45.0%, and a new solution is provided for preparing a high-performance alloy.

Description

Technical Field

[0001] The present invention relates to the technical field of additive manufacturing of metal materials, specifically to a high-strength, hydrogen embrittlement-resistant nickel-based high-temperature alloy and a preparation process thereof, and more specifically to a laser powder bed melted high-strength, hydrogen embrittlement-resistant nickel-based high-temperature alloy and a preparation process thereof. Background Art

[0002] With the rapid development of the hydrogen energy green industry, the demand for high-strength and tough nickel-based high-temperature alloys that are resistant to hydrogen embrittlement for parts serving in hydrogen-containing environments is increasing. Inconel718 nickel-based alloy has obvious advantages in the integrated forming of complex structures in the aerospace field due to its good welding performance and excellent corrosion resistance and mechanical properties at high temperatures.

[0003] Laser powder bed melting technology is an emerging process that has developed rapidly in recent years. It can quickly and accurately manufacture complex structural parts, simplify the process, save materials, and significantly shorten the material research and development cycle. It can realize the manufacture of complex structures that are difficult or impossible to process with traditional processes. The laser powder bed melting process has a fast cooling rate, the strengthening phase fails to precipitate in time, and the fine grains have a typical {001} texture. The comprehensive mechanical properties of the additively manufactured nickel-based high-temperature alloy are not conducive to its service in hydrogen-containing environments. Therefore, it is urgent to optimize the microstructure of 3D printed nickel-based alloys through heat treatment to synergistically improve the strength and hydrogen embrittlement resistance of metal printed parts.

[0004] Inconel718 nickel-based alloy is prone to nucleation of brittle phase and preferential texture due to high cooling rate and element segregation during non-equilibrium solidification. Improving alloy microstructure through heat treatment is the main way to optimize alloy performance. Therefore, improving the crystallographic characteristics of additively manufactured metals through heat treatment is crucial for the design of components serving in hydrogen-containing environments. Summary of the invention

[0005] In order to solve the problems existing in the prior art, the main purpose of the present invention is to provide a laser powder bed melted high-strength hydrogen embrittlement resistant nickel-based high-temperature alloy and a preparation process thereof.

[0006] According to one aspect of the present invention, the present invention provides the following technical solution:

[0007] A preparation process of a high-strength, hydrogen-embrittlement-resistant nickel-based high-temperature alloy by laser powder bed melting, comprising:

[0008] The nickel-based alloy formed by laser powder bed melting is heat treated with a heat treatment process of two-step solid solution + two-stage aging to obtain a high-strength, hydrogen-embrittlement-resistant nickel-based high-temperature alloy.

[0009] As a preferred solution of the preparation process of a laser powder bed melting high-strength hydrogen embrittlement resistant nickel-based high-temperature alloy described in the present invention, the two-step solid solution is:

[0010] The first step is solution temperature of 1000-1100°C, holding time of 0.5-1.5h, and air cooling to room temperature;

[0011] The second step is solution temperature at 930-1030°C, holding time at 0.5-1.5h, and air cooling to room temperature.

[0012] As a preferred solution of the preparation process of a laser powder bed melting high-strength hydrogen embrittlement resistant nickel-based high-temperature alloy described in the present invention, the two-stage aging is:

[0013] The first stage aging temperature is 670-770℃, the holding time is 7-9h, and the furnace is cooled to the second stage aging temperature;

[0014] The second stage aging temperature is 570-670℃, the holding time is 7-9h, and then air-cooled to room temperature.

[0015] As a preferred solution of the laser powder bed melting process for preparing high-strength and hydrogen embrittlement-resistant nickel-based high-temperature alloy described in the present invention, nickel-based alloy powder is selected and a high relative density laser powder bed melting process is adopted to print and form the nickel-based alloy.

[0016] As a preferred scheme of the preparation process of a laser powder bed melting high-strength hydrogen embrittlement-resistant nickel-based high-temperature alloy described in the present invention, the chemical composition of the nickel-based alloy powder is: Cr is 18.30-18.70wt.%, Fe is 19.60-20.00wt.%, Nb is 4.90-5.30wt.%, Mo is 2.90-3.30wt.%, Al is 0.30-0.70wt.%, Ti is 0.80-1.20wt.%, and Ni is the balance; the particle size of the nickel-based alloy powder is: 10-60μm.

[0017] As a preferred scheme of the preparation process of a high-strength, hydrogen-embrittlement-resistant nickel-based high-temperature alloy by laser powder bed melting described in the present invention, the laser powder bed melting process is as follows: the laser power is 270-300 W, the scanning speed is 650-750 mm / s, the scanning spacing is 0.10-0.12 mm, the powder layer thickness is 0.03-0.05 mm, and the interlayer rotation angle is 67°.

[0018] As a preferred solution of the laser powder bed melting process for preparing a high-strength, hydrogen embrittlement-resistant nickel-based high-temperature alloy described in the present invention, the oxygen content in the process chamber of the laser powder bed melting process is 50 to 200 ppm.

[0019] According to another aspect of the present invention, the present invention provides the following technical solution:

[0020] A laser powder bed melted high-strength hydrogen embrittlement resistant nickel-based high-temperature alloy is prepared by adopting the laser powder bed melted high-strength hydrogen embrittlement resistant nickel-based high-temperature alloy preparation process.

[0021] As a preferred solution of the laser powder bed melted high-strength hydrogen embrittlement resistant nickel-based high-temperature alloy described in the present invention, wherein: the relative density of the laser powder bed melted high-strength hydrogen embrittlement resistant nickel-based high-temperature alloy is ≥99.30%.

[0022] As a preferred solution of the laser powder bed melted high-strength hydrogen embrittlement-resistant nickel-based high-temperature alloy described in the present invention, the nickel-based high-temperature alloy includes Inconel718 alloy, Inconel600 alloy, Inconel625 alloy, Inconel690 alloy, and InconelX750 alloy; preferably, the nickel-based high-temperature alloy is Inconel718 alloy.

[0023] As a preferred embodiment of the laser powder bed melted high-strength, hydrogen embrittlement-resistant nickel-based high-temperature alloy described in the present invention, the microstructure of the laser powder bed melted high-strength, hydrogen embrittlement-resistant nickel-based high-temperature alloy includes high-density fine strengthening phases and twins within the crystal, short rod δ phases at the grain boundaries, and low-index grains formed by recrystallization.

[0024] As a preferred solution of the laser powder bed melted high-strength hydrogen embrittlement resistant nickel-based high-temperature alloy described in the present invention, wherein: the laser powder bed melted high-strength hydrogen embrittlement resistant nickel-based high-temperature alloy has a tensile strength of ≥1300MPa and a hydrogen embrittlement sensitivity of ≤45.0%.

[0025] The beneficial effects of the present invention are as follows:

[0026] The present invention proposes a laser powder bed melt high-strength hydrogen embrittlement-resistant nickel-based high-temperature alloy and a preparation process thereof. By designing and optimizing a heat treatment process system, including two-step solid solution and two-stage aging treatment, high-density fine strengthening phases and twins are precipitated in the crystals, and low-index grains and short rod δ phases at the grain boundaries are formed by recrystallization, thereby synergistically improving the strength and hydrogen embrittlement resistance of the nickel-based alloy. The tensile strength of the prepared nickel-based alloy is ≥1300MPa, and the hydrogen embrittlement sensitivity is ≤45.0%, providing a new solution for the preparation of high-performance alloys. BRIEF DESCRIPTION OF THE DRAWINGS

[0027] In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the drawings required for use in the embodiments or the description of the prior art will be briefly introduced below. Obviously, the drawings described below are only some embodiments of the present invention. For ordinary technicians in this field, other drawings can be obtained based on the structures shown in these drawings without paying creative work.

[0028] Figure 1The microstructure diagrams of the nickel-based high-temperature alloys prepared in the embodiments of the present invention and the comparative examples are shown.

[0029] Figure 2 It is a diagram showing the tensile results of the nickel-based high-temperature alloys prepared in the embodiments of the present invention and the comparative examples.

[0030] Figure 3 The graph is a relationship between the strength and hydrogen embrittlement sensitivity of the nickel-based high-temperature alloys prepared in the embodiments of the present invention and the comparative examples.

[0031] Figure 4 The hydrogen-charged fracture crack diagrams of the nickel-based high-temperature alloys prepared in the embodiments of the present invention and the comparative examples are shown.

[0032] The realization of the purpose, functional features and advantages of the present invention will be further explained in conjunction with embodiments and with reference to the accompanying drawings. DETAILED DESCRIPTION

[0033] The following will be described clearly and completely in conjunction with the technical solutions in the embodiments. Obviously, the described embodiments are only part of the embodiments of the present invention, not all of the embodiments. Based on the embodiments of the present invention, all other embodiments obtained by ordinary technicians in this field without creative work are within the scope of protection of the present invention.

[0034] The present invention provides a laser powder bed melt high-strength hydrogen embrittlement resistant nickel-based high-temperature alloy and a preparation process thereof. Since heat treatment can change the microstructure of the laser powder bed melt-formed alloy, high-performance alloys can be prepared according to service requirements. Therefore, the present invention improves the microstructure of the nickel-based alloy by designing and optimizing the heat treatment process, thereby preparing a high-strength hydrogen embrittlement resistant nickel-based high-temperature alloy, which has great significance for practical industrial applications.

[0035] According to one aspect of the present invention, the present invention provides the following technical solution:

[0036] A preparation process of a high-strength, hydrogen-embrittlement-resistant nickel-based high-temperature alloy by laser powder bed melting, comprising:

[0037] The nickel-based alloy formed by laser powder bed melting is heat treated with a heat treatment process of two-step solid solution + two-stage aging to obtain a high-strength, hydrogen-embrittlement-resistant nickel-based high-temperature alloy.

[0038] Preferably, the two-step solid solution is:

[0039] The first step is solution temperature of 1000-1100°C, holding time of 0.5-1.5h, and air cooling to room temperature;

[0040] The second step is solution temperature at 930-1030°C, holding time at 0.5-1.5h, and air cooling to room temperature.

[0041] Specifically, the first step solution temperature can be, for example, any one of 1000°C, 1010°C, 1020°C, 1030°C, 1040°C, 1050°C, 1060°C, 1070°C, 1080°C, 1090°C, 1100°C, or a range between any two of them; the holding time can be, for example, any one of 0.5h, 0.75h, 1h, 1.25h, 1.5h, or a range between any two of them; the second step solution temperature can be, for example, any one of 930°C, 940°C, 950°C, 960°C, 970°C, 980°C, 990°C, 1000°C, 1010°C, 1020°C, 1030°C, or a range between any two of them; the holding time can be, for example, any one of 0.5h, 0.75h, 1h, 1.25h, 1.5h, or a range between any two of them.

[0042] Preferably, the two-stage aging is:

[0043] The first stage aging temperature is 670-770℃, the holding time is 7-9h, and the furnace is cooled to the second stage aging temperature;

[0044] The second stage aging temperature is 570-670℃, the holding time is 7-9h, and then air-cooled to room temperature.

[0045] Specifically, the first-stage aging temperature may be, for example, any one of 670°C, 680°C, 690°C, 700°C, 710°C, 720°C, 730°C, 740°C, 750°C, 760°C, and 770°C, or a range between any two of them; the holding time may be, for example, any one of 7h, 7.5h, 8h, 8.5h, and 9h, or a range between any two of them; the second-stage aging temperature may be, for example, any one of 670°C, 680°C, 690°C, 700°C, 710°C, 720°C, 730°C, 740°C, 750°C, 760°C, and 770°C, or a range between any two of them; the holding time may be, for example, any one of 7h, 7.5h, 8h, 8.5h, and 9h, or a range between any two of them.

[0046] Preferably, before the heat treatment, the method further comprises:

[0047] Laser powder bed fusion forming of nickel-based alloys: Commercial nickel-based alloy powder is selected and a high relative density laser powder bed fusion preparation process is adopted to print and form nickel-based alloys.

[0048] Further preferably, the chemical composition of the commercial nickel-based alloy powder is: Cr is 18.30-18.70wt.%, Fe is 19.60-20.00wt.%, Nb is 4.90-5.30wt.%, Mo is 2.90-3.30wt.%, Al is 0.30-0.70wt.%, Ti is 0.80-1.20wt.%, and Ni is the balance. Specifically, the Cr may be, for example, any one of 18.30wt.%, 18.40wt.%, 18.50wt.%, 18.60wt.%, 18.70wt.%, or any range between two of them; the Fe may be, for example, any one of 19.60wt.%, 19.70wt.%, 19.80wt.%, 19.90wt.%, 20.00wt.%, or any range between two of them; the Nb may be, for example, any one of 4.90wt.%, 5.00wt.%, 5.10wt.%, 5.20wt.%, 5.30wt.%, or any range between two of them. % , 0.50wt.%, 0.60wt.%, 0.70wt.% or any range between the two; Mo may be, for example, 2.90wt.%, 3.00wt.%, 3.10wt.%, 3.20wt.%, 3.30wt.% or any range between the two; Al may be, for example, 0.30wt.%, 0.40wt.%, 0.50wt.%, 0.60wt.%, 0.70wt.% or any range between the two; Ti may be, for example, 0.80wt.%, 0.90wt.%, 1.00wt.%, 1.10wt.%, 1.20wt.% or any range between the two.

[0049] More preferably, the particle size of the commercial nickel-based alloy powder is 10-60 μm. Specifically, the particle size of the powder can be, for example, in the range of any two of 10 μm, 20 μm, 30 μm, 40 μm, 50 μm, and 60 μm.

[0050] Further preferably, the laser powder bed melting process is: laser power is 270-300 W, scanning speed is 650-750 mm / s, scanning spacing is 0.10-0.12 mm, powder layer thickness is 0.03-0.05 mm, and inter-layer rotation angle is 67°. Specifically, the laser power can be, for example, any one of 270W, 280W, 290W, 300W, or a range between any two of them; the scanning speed can be, for example, any one of 650mm / s, 660mm / s, 670mm / s, 680mm / s, 690mm / s, 700mm / s, 710mm / s, 720mm / s, 730mm / s, 740mm / s, 750mm / s, or a range between any two of them; the scanning spacing can be, for example, any one of 0.10mm, 0.11mm, 0.12mm, or a range between any two of them; the powder layer thickness can be, for example, any one of 0.03m, 0.04m, 0.05m, or a range between any two of them.

[0051] Further preferably, the oxygen content in the process chamber of the laser powder bed melting process is 50-200 ppm. Specifically, the oxygen content in the chamber can be, for example, any one of 50 ppm, 100 ppm, 150 ppm, 200 ppm, or a range between any two thereof.

[0052] According to another aspect of the present invention, the present invention provides the following technical solution:

[0053] A laser powder bed melted high-strength hydrogen embrittlement resistant nickel-based high-temperature alloy is prepared by adopting the laser powder bed melted high-strength hydrogen embrittlement resistant nickel-based high-temperature alloy preparation process.

[0054] Preferably, the relative density of the laser powder bed melted high-strength and hydrogen embrittlement resistant nickel-based high-temperature alloy is ≥99.30%. Further preferably, the relative density of the laser powder bed melted high-strength and hydrogen embrittlement resistant nickel-based high-temperature alloy is ≥99.50%, further preferably, the relative density of the laser powder bed melted high-strength and hydrogen embrittlement resistant nickel-based high-temperature alloy is ≥99.80%, further preferably, the relative density of the laser powder bed melted high-strength and hydrogen embrittlement resistant nickel-based high-temperature alloy is ≥99.90%.

[0055] Preferably, the nickel-based high-temperature alloy includes Inconel718 alloy, Inconel600 alloy, Inconel625 alloy, Inconel690 alloy, and InconelX750 alloy; further preferably, the nickel-based high-temperature alloy is Inconel718 alloy.

[0056] Preferably, the microstructure of the laser powder bed melted high-strength hydrogen embrittlement resistant nickel-based high-temperature alloy includes high-density fine strengthening phases and twins within the grains, short rod δ phases at the grain boundaries, and low-index grains formed by recrystallization.

[0057] Preferably, the tensile strength of the laser powder bed melted high-strength hydrogen embrittlement resistant nickel-based high-temperature alloy is ≥1300MPa, and the hydrogen embrittlement sensitivity is ≤45.0%; further preferably, the tensile strength of the laser powder bed melted high-strength hydrogen embrittlement resistant nickel-based high-temperature alloy is ≥1350MPa, and the hydrogen embrittlement sensitivity is ≤40.0%; further preferably, the tensile strength of the laser powder bed melted high-strength hydrogen embrittlement resistant nickel-based high-temperature alloy is 1363MPa, and the hydrogen embrittlement sensitivity is 36.0%.

[0058] The technical solution of the present invention is further described below in conjunction with specific embodiments.

[0059] Example 1

[0060] A preparation process of a high-strength hydrogen embrittlement-resistant Inconel718 nickel-based alloy by laser powder bed melting, comprising:

[0061] Laser powder bed melting of nickel-based alloy: commercial nickel-based alloy powder is selected, and the high relative density laser powder bed melting preparation process is adopted to print and form the nickel-based alloy. The chemical composition of commercial nickel-based alloy powder is: Cr is 18.50wt.%, Fe is 19.80wt.%, Nb is 5.10wt.%, Mo is 3.10wt.%, Al is 0.50wt.%, Ti is 1.00wt.%, and Ni is the balance. The laser powder bed melting process is: laser power is 285W, scanning speed is 700mm / s, scanning spacing is 0.11mm, powder layer thickness is 0.04mm, and interlayer rotation angle is 67°. The oxygen content in the process chamber of the laser powder bed melting process is 100ppm.

[0062] The laser powder bed melted Inconel718 nickel-based alloy was heat treated to obtain high-strength hydrogen embrittlement-resistant Inconel718 nickel-based alloy.

[0063] The specific heat treatment process is as follows: the first step solution temperature is 1050°C, the holding time is 1h, and air cooling to room temperature; the second step solution temperature is 980°C, the holding time is 1h, and air cooling to room temperature; the first stage aging temperature is 720°C, the holding time is 8h, furnace cooling to the second stage aging temperature is 620°C, the holding time is 8h, and air cooling to room temperature. The microstructure of the Inconel718 nickel-based alloy prepared in this embodiment is shown in FIG. Figure 1 (c 1 )-(c 3), which are scanning electron microscope images, transmission electron microscope images and electron backscatter diffraction images, respectively. It can be seen that short rod δ phase is distributed at the grain boundary, the recrystallized grains are low-index, and γ' and γ" strengthening phases are dispersed in the grains.

[0064] Comparative Example 1

[0065] The difference from Example 1 is that

[0066] Without heat treatment, Inconel718 nickel-based high-temperature alloy is obtained, and its microstructure is shown in the figure below. Figure 1 (a 1 )-(a 3 ), which are scanning electron microscope images, transmission electron microscope images and electron backscatter diffraction images, respectively. It can be seen that it contains a large number of dislocation cell structures, Laves harmful phases are distributed at the cell boundaries, and the laser powder bed fusion-formed grains have a typical {100} orientation.

[0067] Comparative Example 2

[0068] The difference from Example 1 is that

[0069] Only one step of solution treatment, the solution temperature is 980℃, and the holding time is 2h; Inconel718 nickel-based high-temperature alloy is obtained, and its microstructure is shown in the figure Figure 1 Middle (b 1 )-(b 3 ), which are scanning electron microscope images, transmission electron microscope images and electron backscatter diffraction images, respectively. It can be seen that there are residual Laves phase and long needle-like δ phase at the grain boundary.

[0070] Comparative Example 3

[0071] The difference from Example 1 is that

[0072] Only one step of solution treatment, the solution temperature is 1150℃, and the holding time is 2h; Inconel718 nickel-based high-temperature alloy is obtained, and its microstructure is shown in the figure Figure 1 Medium (d 1 )-(d 3 ), which are scanning electron microscope images, transmission electron microscope images and electron backscatter diffraction images respectively. It can be seen that (Nb, Ti) C carbides are distributed at the twin boundaries and the grains have grown significantly.

[0073] Figure 2 The tensile results of the nickel-based high-temperature alloys prepared in Example 1 and Comparative Examples 1-3 are shown in FIG. Figure 3 The strength and hydrogen embrittlement sensitivity relationship diagram of the nickel-based high-temperature alloys prepared in Example 1 and Comparative Examples 1-3. Figure 1 (a 2) It can be seen that the comparative example 1 lacks a strengthening phase inside, and the tensile strength is the lowest in the hydrogen-containing environment, which is only 983MPa. The large amount of brittle phases at the grain boundaries of the comparative example 2 are not conducive to its plasticity, and the elongation after fracture of the hydrogen-permeated sample is only 5.7%. As for the comparative example 3, the grain size effect accelerates the cracking, and the hydrogen embrittlement sensitivity is 54.8%; the dispersed strengthening phase within the grains of the Inconel718 nickel-based high-temperature alloy prepared in Example 1 makes its tensile strength 1363MPa, and the low-index recrystallized grains are conducive to dislocation slip during deformation, and the hydrogen embrittlement sensitivity is 36.0%, realizing the preparation of high-strength and hydrogen-embrittlement-resistant nickel-based high-temperature alloy.

[0074] Figure 4 The hydrogen-charged tensile fracture crack diagrams of the nickel-based high-temperature alloys prepared in Example 1 and Comparative Examples 1-3 are shown in FIG. Figure 4 It can be seen that comparative examples 1-3 (such as Figure 4 The cracks of the nickel-based alloy prepared in (a), (b) and (d) mostly extend along the crystal (IG), while the crack tip of Example 1 shows transgranular (TG) fracture, as shown in FIG. Figure 4 As shown in (c), this is attributed to the fact that the low-index grains in Example 1 allow more slip systems to be activated, and the stress concentration of the grain boundary short rod δ phase is relatively small, which is not easy to crack and is conducive to crack redirection. The high strength of Example 1 comes from the dispersed γ' and γ" strengthening phases in the grain, and the hydrogen embrittlement resistance comes from the synergistic effect of the low-index grains and the grain boundary short rod δ phase.

[0075] The above description is only a preferred embodiment of the present invention, and does not limit the patent scope of the present invention. All equivalent structural changes made by using the contents of the present invention specification under the inventive concept of the present invention, or directly / indirectly applied in other related technical fields are included in the patent protection scope of the present invention.

Claims

1. A process for preparing a high-strength, hydrogen-embrittlement-resistant nickel-based high-temperature alloy by laser powder bed melting, characterized in that: include: The nickel-based alloy formed by laser powder bed melting is heat treated with a heat treatment process of two-step solid solution + two-stage aging to obtain a high-strength, hydrogen-embrittlement-resistant nickel-based high-temperature alloy.

2. The process for preparing a high-strength, hydrogen embrittlement-resistant nickel-based high-temperature alloy by laser powder bed melting according to claim 1, characterized in that: The two-step solid solution is: The first step is solution temperature of 1000-1100°C, holding time of 0.5-1.5h, and air cooling to room temperature; The second step is solution temperature of 930-1030°C, holding time of 0.5-1.5h, and air cooling to room temperature.

3. The process for preparing a high-strength, hydrogen embrittlement-resistant nickel-based high-temperature alloy by laser powder bed melting according to claim 1, characterized in that: The two levels of aging are: The first stage aging temperature is 670-770℃, the holding time is 7-9h, and the furnace is cooled to the second stage aging temperature; The second stage aging temperature is 570-670℃, the holding time is 7-9h, and then air-cooled to room temperature.

4. The process for preparing a high-strength, hydrogen embrittlement-resistant nickel-based high-temperature alloy by laser powder bed melting according to claim 1, characterized in that: Nickel-based alloy powder is selected and a high relative density laser powder bed fusion preparation process is adopted to print and form the nickel-based alloy.

5. The process for preparing a high-strength, hydrogen embrittlement-resistant nickel-based high-temperature alloy by laser powder bed melting according to claim 4, characterized in that: The chemical composition of the nickel-based alloy powder is: Cr is 18.30-18.70wt.%, Fe is 19.60-20.00wt.%, Nb is 4.90-5.30wt.%, Mo is 2.90-3.30wt.%, Al is 0.30-0.70wt.%, Ti is 0.80-1.20wt.%, and Ni is the balance; the particle size of the nickel-based alloy powder is: 10-60μm.

6. The process for preparing a high-strength, hydrogen embrittlement-resistant nickel-based high-temperature alloy by laser powder bed melting according to claim 1, characterized in that: The laser powder bed melting process is: laser power is 270-300W, scanning speed is 650-750mm / s, scanning spacing is 0.10-0.12mm, powder layer thickness is 0.03-0.05mm, and interlayer rotation angle is 67°.

7. The process for preparing a high-strength, hydrogen embrittlement-resistant nickel-based high-temperature alloy by laser powder bed melting according to claim 1, characterized in that: The oxygen content in the process chamber of the laser powder bed fusion process is 50 to 200 ppm.

8. A laser powder bed melted high-strength hydrogen embrittlement resistant nickel-based high-temperature alloy, characterized in that: The alloy is prepared by the laser powder bed melting high-strength hydrogen embrittlement-resistant nickel-based high-temperature alloy preparation process described in any one of claims 1 to 7.

9. The laser powder bed melted high-strength hydrogen embrittlement resistant nickel-based high-temperature alloy according to claim 8 is characterized in that: The microstructure of the laser powder bed melted high-strength hydrogen embrittlement resistant nickel-based high-temperature alloy includes high-density fine strengthening phases and twins within the crystal, short rod δ phases at the grain boundaries, and low-index grains formed by recrystallization.

10. The laser powder bed melted high-strength hydrogen embrittlement resistant nickel-based high-temperature alloy according to claim 8 is characterized in that: The relative density of the laser powder bed melted high-strength hydrogen embrittlement resistant nickel-based high-temperature alloy is 99.30%; the laser powder bed melted high-strength hydrogen embrittlement resistant nickel-based high-temperature alloy has a tensile strength of ≥1300MPa and a hydrogen embrittlement sensitivity of ≤45.0%.

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