High-temperature-resistant nickel-based superalloy containing hcl atmosphere corrosion, and preparation method and application thereof

Abstract

The present application relates to the technical field of high-temperature alloy, and particularly relates to a high-temperature corrosion-resistant nickel-based high-temperature alloy containing HCl atmosphere, a preparation method and application thereof. The high-temperature corrosion-resistant nickel-based high-temperature alloy containing HCl atmosphere comprises the following components in percentage by mass: C 0.04%-0.07%, Cr 18%-20%, Mo 3.5%-4.5%, W 4.5%-5%, Al 1.2%-1.8%, Ti 2.3%-2.7%, Si≤0.6%, Mn≤0.5%, Fe≤2%, B≤0.01%, Ce≤0.01%, and the balance of Ni and inevitable impurities. The nickel-based high-temperature alloy has good room-temperature and high-temperature mechanical properties and 1100 DEG C HCl atmosphere corrosion resistance, and can meet the material selection requirements of a new generation of marine engine.

Description

Technical Field

[0001] This invention relates to the field of high-temperature alloy technology, and in particular to a nickel-based high-temperature alloy resistant to corrosion in a high-temperature HCl atmosphere, its preparation method, and its application. Background Technology

[0002] With the continuous improvement of the performance of new-generation marine engines, the operating conditions of their key hot-end components—gas nozzles—are becoming increasingly demanding. In actual service, gas nozzles must withstand extreme temperatures up to 1100℃, while also facing high pressure, high flow rates, and corrosive gases containing HCl. To ensure stable engine operation, the alloy materials used for gas nozzles must not only possess excellent high-temperature mechanical properties at 1100℃, but also have superior resistance to high-temperature HCl corrosion.

[0003] Currently, high-temperature alloys resistant to HCl corrosion are mostly suitable for medium- and low-temperature (below 700℃) operating conditions. However, when the service temperature is increased to 1100℃, the high-temperature mechanical properties of the alloy decrease significantly, and the corrosive effect of the HCl atmosphere on the alloy is significantly aggravated, making it difficult for existing alloys to meet the stringent requirements for the structural integrity and long-term safe service of gas nozzles.

[0004] In view of this, the present invention is hereby proposed. Summary of the Invention

[0005] The purpose of this invention is to provide a nickel-based superalloy resistant to high-temperature corrosion in HCl atmosphere, its preparation method and application. The nickel-based superalloy of this invention has both good room temperature and high temperature mechanical properties as well as resistance to corrosion in HCl atmosphere at 1100℃, which can meet the material selection requirements of the new generation of marine engines.

[0006] To achieve the above-mentioned objectives of the present invention, a first aspect of the present invention provides a nickel-based superalloy resistant to corrosion in a high-temperature HCl atmosphere, comprising the following components by mass percentage: C 0.04%~0.07%, Cr 18%~20%, Mo 3.5%~4.5%, W 4.5%~5%, Al 1.2%~1.8%, Ti 2.3%~2.7%, Si≤0.6%, Mn≤0.5%, Fe≤2%, B≤0.01%, Ce≤0.01%, with the balance being Ni and unavoidable impurities.

[0007] In a specific embodiment of the present invention, the content of C element in the nickel-based superalloy resistant to high-temperature corrosion in HCl atmosphere is 0.04%~0.06%, preferably 0.05%~0.06%.

[0008] In a specific embodiment of the present invention, the content of Mo element in the nickel-based superalloy resistant to high-temperature corrosion in HCl atmosphere is 3.8% to 4.5%, preferably 4% to 4.5%.

[0009] In a specific embodiment of the present invention, the content of Ti element in the nickel-based superalloy resistant to high-temperature corrosion in HCl atmosphere is 2.4% to 2.7%, preferably 2.5% to 2.7%.

[0010] In a specific embodiment of the present invention, the Cr content in the nickel-based superalloy resistant to high-temperature corrosion in HCl atmosphere is 18%~19.5%, preferably 18%~19%.

[0011] In a specific embodiment of the present invention, the room temperature tensile properties of the nickel-based superalloy resistant to corrosion in a high-temperature HCl atmosphere meet the following requirements: tensile strength ≥ 1150 MPa, yield strength ≥ 650 MPa, elongation after fracture ≥ 25%, and reduction of area after fracture ≥ 25%.

[0012] In a specific embodiment of the present invention, the tensile properties of the nickel-based superalloy resistant to corrosion in a high-temperature HCl atmosphere at 1100℃ meet the following requirements: tensile strength ≥70MPa, yield strength ≥50MPa, elongation after fracture ≥85%, and reduction of area after fracture ≥50%.

[0013] The second aspect of this invention provides a method for preparing the nickel-based superalloy resistant to high-temperature corrosion in an HCl atmosphere provided in the first aspect of this invention, comprising the following steps: (a) Ingots are prepared by vacuum induction melting and vacuum consumable melting; (b) The ingot is homogenized and then forged.

[0014] In a specific embodiment of the present invention, the homogenization treatment includes: heat treatment at 1150~1165℃ for 10~14h, and then heat treatment at 1180~1200℃ for 46~50h.

[0015] The third aspect of the present invention provides the application of the nickel-based superalloy resistant to high-temperature corrosion in HCl atmosphere provided in the first aspect of the present invention or the nickel-based superalloy resistant to high-temperature corrosion in HCl atmosphere prepared by the preparation method provided in the second aspect of the present invention in the preparation of gas nozzles.

[0016] Compared with the prior art, the beneficial effects of the present invention are as follows: This invention designs and controls the elemental composition of nickel-based superalloys, including Cr, Al, W, C, Mo, Ti, and Fe, to enable the alloy to possess excellent mechanical properties and corrosion resistance at 1100℃ in an HCl-containing atmosphere, thus meeting the material selection requirements for next-generation marine engines. Attached Figure Description

[0017] To more clearly illustrate the specific embodiments of the present invention or the technical solutions in the prior art, the drawings used in the description of the specific embodiments or the prior art will be briefly introduced below. Obviously, the drawings described below are some embodiments of the present invention. For those skilled in the art, other drawings can be obtained from these drawings without creative effort.

[0018] Figure 1 A schematic diagram of the working principle of the experimental equipment used for corrosion resistance performance testing in an experimental example of the present invention; Figure 2 This is a macroscopic photograph of the nickel-based superalloy sample provided in Example 1 of the present invention before corrosion resistance testing; Figure 3 This is a macroscopic photograph of the nickel-based superalloy sample provided in Example 1 of the present invention after corrosion resistance testing; Figure 4 The image shows the microstructure of the nickel-based superalloy sample provided in Example 1 of this invention after corrosion resistance testing. Figure 5 This is a longitudinal section EPMA microstructure image of the nickel-based superalloy sample provided in Example 1 of the present invention after corrosion resistance testing; Figure 6 The longitudinal section EPMA microstructure of the nickel-based superalloy sample provided for Comparative Example 5 after corrosion resistance testing. Detailed Implementation

[0019] The technical solution of the present invention will be clearly and completely described below with reference to the accompanying drawings and specific embodiments. However, those skilled in the art will understand that the embodiments described below are some embodiments of the present invention, but not all embodiments, and are only used to illustrate the present invention, and should not be regarded as limiting the scope of the present invention. Based on the embodiments of the present invention, all other embodiments obtained by those skilled in the art without creative effort are within the scope of protection of the present invention. Where specific conditions are not specified in the embodiments, conventional conditions or conditions recommended by the manufacturer shall be followed. Where the manufacturers of reagents or instruments are not specified, they are all conventional products that can be purchased commercially.

[0020] The first aspect of this invention provides a nickel-based superalloy resistant to corrosion in a high-temperature HCl atmosphere, comprising the following components by mass percentage: C 0.04%~0.07%, Cr 18%~20%, Mo 3.5%~4.5%, W 4.5%~5%, Al 1.2%~1.8%, Ti 2.3%~2.7%, Si≤0.6%, Mn≤0.5%, Fe≤2%, B≤0.01%, Ce≤0.01%, with the balance being Ni and unavoidable impurities.

[0021] This invention designs and controls the elemental composition of nickel-based superalloys, including Cr, Al, W, C, Mo, Ti, and Fe, to enable the alloy to possess excellent mechanical properties and corrosion resistance at 1100℃ in an HCl-containing atmosphere, thus meeting the material selection requirements for next-generation marine engines.

[0022] The inventors of this invention discovered in their research that Cr, Al, and W elements are beneficial for improving the alloy's resistance to corrosion in high-temperature HCl atmospheres, while C, Mo, Ti, and Fe elements are detrimental to improving the alloy's resistance to corrosion in high-temperature HCl atmospheres.

[0023] Specifically, the alloy strengthening methods of this invention are solid solution strengthening and age hardening. Al and W elements can improve the corrosion resistance of the alloy and also improve its high-temperature strength, so the content of Al and W elements should be increased as much as possible. However, excessive Al elements will significantly reduce the processability of the alloy, and excessive W elements will increase the tendency for harmful phases to precipitate in the alloy. Therefore, in the specific embodiments of this invention, the Al element content is 1.2%~1.8%, specifically 1.2%, 1.3%, 1.4%, 1.5%, 1.6%, 1.7%, 1.8%, or any combination thereof; the W element content is 4.5%~5%, specifically 4.5%, 4.6%, 4.7%, 4.8%, 4.9%, 5%, or any combination thereof. This is more conducive to improving the alloy's resistance to high-temperature corrosion in HCl atmospheres while ensuring the alloy's high-temperature strength and processability.

[0024] In a specific embodiment of the present invention, the Cr content in the nickel-based superalloy resistant to high-temperature corrosion in an HCl atmosphere is 18%~20%, specifically within the range of 18%, 18.2%, 18.5%, 18.8%, 19%, 19.2%, 19.5%, 19.8%, 20%, or any combination thereof, preferably 18%~19.5%, more preferably 18%~19%. Controlling the Cr content within the above range helps Cr preferentially form a dense, continuous, and thermodynamically stable Cr2O3 protective film at 1100℃ in an HCl atmosphere, effectively blocking HCl corrosion; simultaneously, it avoids excessively high Cr content leading to the precipitation of brittle σ phase, which would deteriorate the alloy's structural stability and mechanical properties. If the Cr content is too low, it is difficult to form a complete and dense oxide film at 1100℃, leading to accelerated alloy corrosion; if the Cr content is too high, it is detrimental to the alloy's thermal strength and long-term structural stability.

[0025] In the alloy of this invention, Mo and Ti elements are detrimental to improving the alloy's corrosion resistance, therefore, the content of Mo and Ti elements should be minimized. However, excessively low levels of Mo and Ti elements will cause the alloy's thermal strength to fail to meet service requirements. Therefore, in a specific embodiment of this invention, the content of Mo element is 3.5% to 4.5%, specifically within the range of 3.5%, 3.6%, 3.7%, 3.8%, 3.9%, 4%, 4.1%, 4.2%, 4.5%, or any combination thereof, preferably 3.8% to 4.5%, more preferably 4% to 4.5%; the content of Ti element is 2.3% to 2.7%, specifically within the range of 2.3%, 2.35%, 2.4%, 2.45%, 2.5%, 2.55%, 2.6%, 2.65%, 2.7%, or any combination thereof, preferably 2.4% to 2.7%, more preferably 2.5% to 2.7%. By appropriately controlling the content of Mo and Ti elements, sufficient solid solution strengthening and age-hardening effects are ensured while minimizing the adverse effects on corrosion resistance. This allows the alloy to maintain good thermal strength at 1100℃, meeting the service mechanical requirements of the gas nozzle. If the Mo and Ti content is too low, the high-temperature strength of the alloy will decrease significantly; if the Mo and Ti content is too high, it will negatively impact the alloy's corrosion resistance in an HCl-containing atmosphere.

[0026] In alloys, carbides are distributed at grain boundaries or within grains. A high carbon content leads to continuous distribution of grain boundary carbides, resulting in decreased corrosion resistance and impaired toughness, plasticity, and structural stability. However, excessively low carbon content is detrimental to the alloy's mechanical properties. Therefore, in specific embodiments of this invention, the carbon content is 0.04% to 0.07%, specifically within the range of 0.04%, 0.045%, 0.05%, 0.052%, 0.055%, 0.058%, 0.06%, 0.065%, 0.07%, or any combination thereof, preferably 0.04% to 0.06%, and more preferably 0.05% to 0.06%.

[0027] Fe readily forms FeCl2 or FeCl3 at high temperatures in an HCl-containing atmosphere. These two chlorination products have low saturated vapor pressures and are easily volatilized at high temperatures, which accelerates the corrosion rate of the alloy. Therefore, in specific embodiments of this invention, the Fe content does not exceed 2%, and can specifically be 2%, 1.95%, 1.9%, 1.85%, 1.8%, 1.75%, 1.7%, 1.6%, 1.5%, 1.2%, 1%, 0.8%, 0.5%, 0.2%, 0.1%, 0.01%, 0.001%, or any combination thereof, for example, 0.001% to 2%.

[0028] In a specific embodiment of the present invention, the content of Si element does not exceed 0.6%, specifically it can be 0.6%, 0.4%, 0.2%, 0.1%, 0.05%, 0.03%, 0.02%, or any combination thereof; the content of Mn element does not exceed 0.5%, specifically it can be 0.5%, 0.4%, 0.3%, 0.2%, 0.1%, 0.08%, 0.06%, 0.04%, 0.02%, or any combination thereof; the content of B element does not exceed 0.01%, specifically it can be 0.01%, 0.008%, 0.007%, 0.005%, 0.003%, or any combination thereof; the content of Ce element does not exceed 0.01%, specifically it can be 0.01%, 0.008%, 0.006%, 0.004%, 0.002%, 0.001%, or any combination thereof.

[0029] In a specific embodiment of the present invention, the room temperature tensile properties of the nickel-based superalloy resistant to corrosion in a high-temperature HCl atmosphere satisfy the following: Tensile strength ≥1150MPa, specifically it can be 1150MPa, 1155MPa, 1160MPa, 1165MPa, 1170MPa, 1176MPa or any combination thereof; Yield strength ≥ 650 MPa, specifically it can be a range of 650 MPa, 660 MPa, 670 MPa, 680 MPa, 690 MPa, 701 MPa or any combination thereof; The elongation after fracture is ≥25%, specifically it can be a range of 25%, 26%, 27%, 28%, 29%, 30%, 30.5% or any two of them; The post-fracture shrinkage rate is ≥25%, specifically it can be 25%, 26%, 27%, 28%, 29%, 30%, 31% or any combination thereof.

[0030] In a specific embodiment of the present invention, the tensile properties of the nickel-based superalloy resistant to corrosion in a high-temperature HCl atmosphere at 1100℃ satisfy the following: Tensile strength ≥ 70MPa, specifically 70MPa, 71MPa, 72MPa, 73MPa, 74MPa, 75MPa or any combination thereof; Yield strength ≥ 50MPa, specifically 50MPa, 50.5MPa, 51MPa, 51.5MPa, 52MPa, 52.5MPa, 53MPa, 54MPa, 55MPa or any combination thereof; The elongation after fracture is ≥85%, specifically it can be a range of 85%, 86%, 87%, 88%, 89%, 90%, 91%, 91.5% or any two of them; The post-fracture shrinkage rate is ≥50%, specifically it can be 50%, 50.5%, 51%, 51.5%, 52%, 52.5%, 53%, 54%, 55% or any combination thereof.

[0031] In a specific embodiment of the present invention, the nickel-based superalloy resistant to high-temperature corrosion in an HCl atmosphere undergoes a weight change of no more than 7 g / m² after corrosion treatment at 1100°C in an atmosphere containing 5% HCl for 3600 s. 2 Specifically, it can be 7g / m 2 6.9g / m 2 6.8g / m 2 6.7g / m 2 6.6g / m 2 6.5g / m 2 6.4g / m 2 6.3g / m 2 6.2g / m 2 6.1g / m 2 6g / m 2Or a range consisting of any two of these. Wherein, the weight change Δm = (m0 - m1) / S, m0 is the initial mass of the alloy, m1 is the mass of the alloy after corrosion treatment, and S is the initial corrosion surface area of ​​the alloy. In the above corrosion treatment test, the smaller the weight change, the better the alloy's resistance to corrosion in an HCl-containing atmosphere at 1100℃; conversely, the larger the weight change, the worse the alloy's resistance to corrosion in an HCl-containing atmosphere at 1100℃.

[0032] The second aspect of this invention provides a method for preparing the nickel-based superalloy resistant to high-temperature corrosion in an HCl atmosphere provided in the first aspect of this invention, comprising the following steps: (a) Ingots are prepared by vacuum induction melting and vacuum consumable melting; (b) The ingot is homogenized and then forged.

[0033] Vacuum induction melting and vacuum consumable melting can be performed according to conventional procedures. For example, the melting temperature for vacuum induction melting is 1500~1550℃ (e.g., 1520℃), the melting time is not less than 90 minutes, and the refining vacuum degree is ≤5Pa; the voltage for vacuum consumable melting is 21~25V (e.g., 23V), the current is 4.5~5.5kA (e.g., 5kA), and the melting rate is 3.5~4.2kg / min (e.g., 3.8kg / min). Specific implementation examples are provided below.

[0034] In a specific embodiment of the present invention, the homogenization treatment includes: holding at 1150~1165℃ for 10~14 hours, followed by holding at 1180~1200℃ for 46~50 hours. In different embodiments, the homogenization treatment may first be performed at 1150℃, 1155℃, 1160℃, 1165℃, or any temperature between these two values ​​for 10 hours, 11 hours, 12 hours, 13 hours, 14 hours, etc., followed by holding at any temperature between 1180℃, 1185℃, 1190℃, 1195℃, 1200℃ for 46 hours, 47 hours, 48 ​​hours, 49 hours, 50 hours, etc. The homogenization treatment of the present invention helps improve the uniformity of the alloy's microstructure and reduce the degree of segregation.

[0035] In a specific embodiment of the present invention, the heating temperature during the forging process is 1100~1120℃, and the final forging temperature is ≥920℃. Further, the deformation per forging pass is 20%~40%, specifically within the range of 20%, 25%, 30%, 35%, 40%, or any combination thereof.

[0036] In a specific embodiment of the present invention, the forging process includes upset forging, such as including but not limited to two upsets and two draws.

[0037] The third aspect of the present invention provides the application of the nickel-based superalloy resistant to high-temperature corrosion in HCl atmosphere provided in the first aspect of the present invention or the nickel-based superalloy resistant to high-temperature corrosion in HCl atmosphere prepared by the preparation method provided in the second aspect of the present invention in the preparation of gas nozzles.

[0038] Example 1 Example 1 provides a nickel-based superalloy resistant to corrosion in a high-temperature HCl atmosphere and its preparation method. Specifically, the nickel-based superalloy resistant to corrosion in a high-temperature HCl atmosphere is prepared using raw materials with the compositions and contents listed in Table 1. The preparation method includes the following steps: (1) Alloy ingots were prepared by conventional vacuum induction melting and vacuum consumable melting according to the alloy composition in Table 1.

[0039] (2) The alloy ingot is held at 1155℃ for 12 hours and then held at 1190℃ for 48 hours. Then it is upsetting twice and drawing twice (initial forging temperature is 1110℃, final forging temperature is ≥920℃), and the deformation of each forging is controlled at 30%±2%.

[0040] (3) The alloy forgings obtained in step (2) are kept at 1080~1120℃ (e.g. 1100℃) for 1 hour and then air-cooled, and then kept at 840~870℃ (e.g. 855℃) for 10 hours and then air-cooled.

[0041] Table 1. Composition of the alloy in Example 1 (mass percentage)

[0042] Comparative Examples 1-5 Comparative Examples 1 to 5 were prepared using the same method as in Example 1, except that the alloy composition was different.

[0043] The alloy compositions of Comparative Examples 1 to 5 are shown in Table 2.

[0044] Table 2. Composition of alloys with different comparative proportions (mass percentage)

[0045] Experimental Example The tensile properties of the alloys prepared in different embodiments and comparative examples were tested, and the test results are shown in Table 3.

[0046] Table 3. Tensile properties of different alloys at room temperature and 1100℃

[0047] Corrosion resistance test specimens (10mm×10mm×50mm, with a 10mm×50mm corroded surface, polished to 2.5μm) were prepared according to the methods of the examples and comparative examples, respectively. The corrosion resistance performance was then tested according to the following procedure, and the test results are shown in Table 4. (1) Sample preparation: Sonicate the corrosion resistance test sample with water and alcohol for 10 minutes each to ensure that the surface oil is cleaned. Weigh and record the cleaned sample (mass is m0).

[0048] (2) According to Figure 1 The working principle diagram shown below illustrates the setup of the experimental equipment. For details, please refer to the following; any aspects not mentioned should follow standard procedures in this field. Air is supplied to the gas generator through an air supply regulation system, and natural gas is supplied to the gas generator through a natural gas supply regulation system. The gas generator then burns the gas to produce high-temperature gas. The high-temperature and high-pressure gas is divided into two paths. One path passes through the gas bypass regulation system, is cooled and regulated before being vented. The other path passes through a mixer, is mixed with hydrogen chloride supplied by the hydrogen chloride supply system, and then supplies gas to the test specimen. After passing through the test piece, the high-temperature mixed gas enters the exhaust gas treatment system for cooling. The alkaline medium in the alkaline tank neutralizes and absorbs the hydrogen chloride, and then the exhaust gas is regulated and discharged into the atmosphere. The cooling water supply regulation system provides cooling spray water to the coolers in the gas bypass regulation system and the exhaust gas treatment system; The measurement and control system is responsible for controlling the actuation valves of the entire system, and at the same time collecting and recording all test data such as pressure, flow rate, and temperature.

[0049] Then turn on the control power switch, check and connect the air, natural gas, and hydrogen chloride supply lines, ensuring that all lines are in normal working order. Open the air line valve, close the exhaust gas valve, and check the airtightness of the lines.

[0050] (3) Under good airtightness, slowly open the exhaust valve; at the same time, open the air pipeline valve, natural gas pipeline valve and hydrogen chloride pipeline valve in sequence, and adjust the flow rate of each gas to the specified value (air flow rate 12g / s, natural gas flow rate 0.3g / s, hydrogen chloride flow rate 8.2g / s).

[0051] (4) Close the natural gas pipeline valve and the hydrogen chloride pipeline valve; turn on the igniter after 1 minute, and then quickly open the natural gas pipeline valve. At this time, observe and record whether the temperature of the temperature sensor on the device rises rapidly. If it rises rapidly, the ignition is successful. If there is no change, you need to repeat step (4) to re-ignite until you observe a rapid temperature change.

[0052] (5) Open the hydrogen chloride pipeline valve to introduce hydrogen chloride gas into the pipeline (the gas composition of the experimental system, by volume fraction, is: HCl 5%, nitrogen 75%, oxygen 10%, carbon dioxide 5%, water vapor (produced by combustion) 5%, and the experimental temperature is 1100℃), and start timing. When the test time reaches 3600s, close the hydrogen chloride pipeline valve, natural gas pipeline valve, and air pipeline valve in sequence, and then quickly open the nitrogen purging pipeline valve to cool the sample and prevent it from undergoing a high-temperature oxidation reaction; after the thermocouple shows a temperature below 400℃, close the nitrogen purging pipeline valve, and then remove the sample; turn off the power.

[0053] (6) Weigh and record the sample after corrosion (mass is m1), and calculate the weight change before and after corrosion according to △m=(m0-m1) / S; where S is the initial corrosion surface area of ​​the sample.

[0054] Table 4. Test results of corrosion resistance of different alloys

[0055] Figure 2 and Figure 3 These are macroscopic photographs of the nickel-based superalloy sample provided in Example 1 of the present invention before and after corrosion resistance testing; Figure 4 SEM image of the microstructure of the nickel-based superalloy sample after corrosion resistance testing provided in Example 1 of this invention. Figure 5 and Figure 6 The images show the longitudinal section EPMA microstructure of the nickel-based superalloy samples provided in Example 1 and Comparative Example 5 after corrosion resistance testing. The nickel-based superalloy in Example 1 showed a relatively smooth surface after corrosion, without obvious corrosion product protrusions or depressions. According to... Figure 5 The longitudinal section morphology of the corrosion sample showed that a dense oxide layer formed on the substrate surface, preventing further corrosion of the substrate by HCl, and no chlorides were found. (Comparison) Figure 6 It can be clearly seen that the nickel-based superalloy of Comparative Example 5 has a distinct chlorination product layer after corrosion, which further indicates that the alloy of the present invention has good mechanical properties and corrosion resistance at 1100℃ in an HCl atmosphere, and can meet the material selection requirements of the new generation of marine engines.

[0056] Finally, it should be noted that the above embodiments are only used to illustrate the technical solutions of the present invention, and not to limit them; although the present invention has been described in detail with reference to the foregoing embodiments, those skilled in the art should understand that modifications can still be made to the technical solutions described in the foregoing embodiments, or equivalent substitutions can be made to some or all of the technical features; and these modifications or substitutions do not cause the essence of the corresponding technical solutions to deviate from the scope of the technical solutions of the embodiments of the present invention.

Claims

1. A nickel-based superalloy resistant to corrosion in a high-temperature HCl atmosphere, characterized in that, Includes the following components by mass percentage: C 0.04%~0.07%, Cr 18%~20%, Mo 3.5%~4.5%, W 4.5%~5%, Al 1.2%~1.8%, Ti 2.3%~2.7%, Si≤0.6%, Mn≤0.5%, Fe≤2%, B≤0.01%, Ce≤0.01%, with the balance being Ni and unavoidable impurities.

2. The nickel-based superalloy resistant to high-temperature corrosion in HCl atmosphere according to claim 1, characterized in that, In the nickel-based superalloy resistant to corrosion in a high-temperature HCl atmosphere, the content of carbon element is 0.04%~0.06%, preferably 0.05%~0.06%.

3. The nickel-based superalloy resistant to corrosion in a high-temperature HCl atmosphere according to claim 1, characterized in that, In the nickel-based superalloy resistant to corrosion in a high-temperature HCl atmosphere, the content of Mo is 3.8% to 4.5%, preferably 4% to 4.5%.

4. The nickel-based superalloy resistant to corrosion in a high-temperature HCl atmosphere according to claim 1, characterized in that, In the nickel-based superalloy resistant to corrosion in a high-temperature HCl atmosphere, the content of Ti element is 2.4%~2.7%, preferably 2.5%~2.7%.

5. The nickel-based superalloy resistant to corrosion in a high-temperature HCl atmosphere according to claim 1, characterized in that, The nickel-based superalloy resistant to corrosion in a high-temperature HCl atmosphere contains 18% to 19.5% Cr, preferably 18% to 19%.

6. The nickel-based superalloy resistant to corrosion in a high-temperature HCl atmosphere according to claim 1, characterized in that, The room temperature tensile properties of the nickel-based superalloy resistant to corrosion in a high-temperature HCl atmosphere meet the following requirements: tensile strength ≥ 1150 MPa, yield strength ≥ 650 MPa, elongation after fracture ≥ 25%, and reduction of fracture ≥ 25%.

7. The nickel-based superalloy resistant to high-temperature corrosion in HCl atmosphere according to claim 1, characterized in that, The high-temperature resistant nickel-based superalloy with HCl atmosphere corrosion has the following tensile properties at 1100℃: tensile strength ≥70MPa, yield strength ≥50MPa, elongation after fracture ≥85%, and reduction of fracture ≥50%.

8. The method for preparing the nickel-based superalloy resistant to corrosion in a high-temperature HCl atmosphere as described in any one of claims 1 to 7, characterized in that, Includes the following steps: (a) Ingots are prepared by vacuum induction melting and vacuum consumable melting; (b) The ingot is homogenized and then forged.

9. The preparation method according to claim 8, characterized in that, The homogenization treatment includes: heat treatment at 1150~1165℃ for 10~14h, and then heat treatment at 1180~1200℃ for 46~50h.

10. The application of the nickel-based superalloy resistant to high-temperature corrosion in HCl atmosphere as described in any one of claims 1 to 7, or the nickel-based superalloy resistant to high-temperature corrosion in HCl atmosphere prepared by the preparation method described in any one of claims 8 to 9, in the preparation of gas nozzles.

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