UA70300C2 - An article cast under pressure and a method for making the same - Google Patents

Abstract

The invention relates to the metallurgy , in particular to making articles of superalloy based on nickel IN 718 and article of gas-turbine engine. A method for making article of gas-turbine engine involves casting the article under pressure, hot isostatic pressing the obtained article at the temperature of 982 - 1023 °С and pressure of 105 - 175 MPa during at least 4 hours. The method allows to obtain practically porouless article which material has a value of liquation no more than 40% and average grain size according to АSТМ equal to3 or less.

Description

Description of the invention

Previous level. 2 This invention relates generally to parts made of superalloy material and relates in particular to parts made of nickel-based superalloys and methods of heat treating such alloys. Such alloys usually have high melting temperatures, more than 1260-13717C (2300-2500). Nickel-based superalloys are used in applications where high strength-to-weight ratios, high corrosion resistance, and in applications where they are used at relatively high temperatures, such as up to or greater than 70 approximately 10932C (20002E), are required.

In gas turbine engines, for example, such superalloys are commonly used in the turbine section and sometimes in the final stages of the compressor section of the engine, which include, but are not limited to, profiles such as vanes and guide vanes, as well as fixed parts and structural elements, such as intermediate and compressor casings, compressor discs, turbine casings and turbine discs. A common nickel-based superalloy 72 used in gas turbine engines is Ipsope! 718 (IM 718), which generally has a composition, in weight percent: approximately 0.01-0.05 carbon (C), 13-25 chromium (Sg), 2.5-3.5 molybdenum (Mo), 5, 0-5.75 (columbium (SB) (also called niobium (MB) | tantalum (TA)), 0.7-1.2 titanium (Ti), 0.3-0.9 aluminum (AI), up to approx. 21 iron (Re), the rest - practically Mi.

In the production of gas turbine engines, forging is used to manufacture parts that have complex three-dimensional shapes, such as vanes and vanes of the directional device. Nickel-based superalloys have traditionally been machined by precision forging to produce parts that have a small average grain size and balance high strength, low weight, and adequate multi-cycle fatigue resistance. When properly manufactured, these parts exhibit a balanced ratio of high strength, long-lasting durability, and low weight. s 29 Briefly, in order to forge a part such as a vane or guide vane, Ho) first obtains a cast material having a composition corresponding to the desired composition of the already manufactured part. The ingot is turned into a properly shaped billet, usually cylindrical for vanes and guide vanes, and is then subjected to thermomechanical treatment, such as heating and stamping several times using dies and/or hammers, which can then be heated and reshaped, at 30 gradually bringing it closer to the desired shape so that the material plastically deforms and smoothly takes the desired shape of the part. Each part is usually heat treated to obtain the required properties, such as hardening/hardening, stress reduction, crack resistance, and a specific level of multi-cycle fatigue resistance, and then it also undergoes a final treatment, "3 for example by machining , chemical treatment, and/or proofing in environments necessary 325 to give the part precise shape, dimensions, or properties. -

The production of parts by forging requires a lot of money and time, and therefore it is used only for parts that require a certain balance of properties, for example, high strength, long-term strength and low weight, both at room temperature and at elevated temperatures. As for obtaining material for forging, certain materials require a long production cycle, which sometimes lasts several months. C 70 Forging usually involves a number of operations, each of which requires separate dies and associated equipment. c Finishing operations after forging, for example, machining the blade shank and surface finishing

Of appropriate quality, require a significant part of all funds for the production of forged parts, and after these operations, a significant part of the parts is rejected.

During the forging of parts, most of the starting material (up to about 8595) is removed and does not form part of the manufactured part, that is, it constitutes production waste. The complexity of the shape of the part that 7 produces only requires the additional effort and cost required to produce the part that is the most av | characteristic of gas turbine engine parts that have particularly complex shapes. Nickel-based superalloys such as IM 718 also exhibit significant spring effect, for example if the material is springy, and spring effect must be taken into account during forging, i.e. parts should usually be "over-forged". How aw! 20 mentioned above, the parts made may still require additional processing after forging. In addition, if computer programs are used to provide calculated flow dynamics in order to analyze and obtain profile shapes with more effective aerodynamic properties, then such profiles and parts have even more complex three-dimensional shapes. Consequently, it is more difficult or impossible to accurately forge superalloys into these advanced, more complex shapes, for example, due in part to the somewhat elastic nature that many materials exhibit during forging, which in turn requires additional

GF) funds for the production of parts or gives the parts such a value that, from the point of view of economy, it is impossible to apply certain advances in engine technology or the use of certain alloys for some parts is completely impractical. Forged parts also often exhibit a significant amount of defects, which include inclusions and carbides, which vary greatly from part to part. Parts with a higher content of niobium, 60 for example, IM 718, are also characterized by natural liquation, as well as the formation of phases, such as Laves phases, and other topologically close packing phases. The presence and number of these defects adversely affects the mechanical properties, especially at elevated temperatures. The number of these defects usually depends on the composition of the material and the length of time when the part is exposed to elevated temperatures, for example during forging.

Therefore, parts are subjected to heat treatment to reduce or eliminate defects, for example, heat treatment for homogenization, which becomes a separate step that is additional to any other processing steps performed in the manufacture of parts. Heat treatment usually involves exposing the part to a relatively high temperature, for example about 10937 (20007) for several hours. This temperature is high enough to reduce curing, but not so high or prolonged that significant grain growth occurs.

Casting was widely used for the production of parts with a relatively almost finished shape.

For the production of such parts, it is possible to use precision casting based on molten models, in which molten metal is poured into a ceramic shell that has a cavity in the shape of the part to be cast.

However, precision casting from molten models produces parts that have extremely large grains (compared to the small average grain size that can be obtained from forging), and in some 7/0 cases the entire part consists of a single crystal. In addition, the rate of solidification can cause the presence of natural liquation in an unacceptable amount, which causes a large spread in the test results (they are different for different parts), or can cause the presence of brittle phases, which also cause deterioration of properties. In addition, due to the fact that a separate model is produced for each part, this method requires a lot of money. From part to part, it is difficult to achieve reproducibility of very precise dimensions. In addition, 7/5 Because the molten metal melts, pours and/or solidifies in air or in the presence of another gas, parts with undesirable properties such as inclusions and porosity are obtained, especially for materials containing chemically active elements . Porosity should be destroyed, for example, by heating the part and applying pressure to the part. Parts from IM 718 during hot isostatic pressing are usually exposed to a temperature between 982-10247C (1800-1875) at a pressure between 105-154MPa (15-22K8i (thousand pounds of force per square inch)) 2o for several hours. The chipping of particles from the ceramic shell also causes the presence of inclusions and impurities in cast parts.

Mold casting, in which the molten material is poured into a reusable multi-section mold and flows into the mold only under the influence of gravity, has also been used for casting parts in general. See, for example, U.S. Patent No. 5,505,246, author So/mip. However, mold casting has some disadvantages. For thin castings such as profiles, the force of gravity may not be sufficient to advance the material into thinner sections, especially where materials with high melting temperatures and low superheats are used, resulting in the mold not being completely filled, causing parts to be rejected. The dimensional tolerance should be relatively large, and it needs correspondingly more significant processing after pouring, and it is difficult to achieve repeatability. As a result of casting in a mold, the final surface of the part is not perfect, which also requires more additional processing after casting.

Die casting, in which a molten material is crimped under pressure into a reusable mold, has been used successfully in the past to create such parts from materials with relatively low melting points (Tt), e.g. Tt below about 10937 (2000).

One type of injection molding machine is described in US Pat. No. 3,791,440 (by Stgovv). In this patent, the machine includes a fixed element 11 of the mold and a movable element 12 of the mold. Briefly speaking, the molten metal is poured through the inlet chute 22 and the vertical pouring channel 21 and flows into the discharge cylinder 30, which communicates with the cavity 15 of the mold. A sufficient amount of molten material is poured in so as to fill the discharge cylinder ZO and part of the vertical pouring channel 21, thereby forcing air out of the discharge cylinder. See, for example, column 6 lines 7-17. The discharge plunger Z8 forces the material to move from the discharge cylinder 30 into the cavity 15 of the mold. The cylinder blocking the vertical downspout and the associated plunger 35 can seal the vertical downspout. channel 21, for example, during injection. The discharge cylinder ZO is surrounded by one of the form plates, which allows prevent cylinder deformation when molten material with a high melting point is poured into the discharge cylinder. In the machine proposed by Stozvyem, a vacuum environment is not used, but the cylinder is completely filled in order to prevent air from being forced into the mold. - And such machines are expensive, besides, such a machine cannot be easily created, and therefore, its renewal and repair, if necessary, require a lot of money. For example, in the best case scenario, it would be difficult and expensive to attach the vacuum system to the machine because the sleeve is surrounded by a plate, making it difficult to access. In addition, in the best case, it will be difficult to move the molten material from the device where the material 5p is melted to the inlet chute 22 under vacuum conditions. It will also be difficult to regulate the temperature of the mold, which is determined not only by the physical size of the assembly, which consists of the plate and the mold surrounded by it, but also by the thermal mass of such an assembly. It will also be difficult to implement such a node in a machine configuration that has a vacuum environment.

Another type of die casting machine is the "cold chamber" type of machine. As described in, for example, U.S. Patent Nos. 2,932,865, 3,106,002, 3,532,561, and 3,646,990, a conventional "cold chamber" injection molding machine includes a loading sleeve attached to one (of course

F) stationary) plate of a multi-section form, for example, to a two-section form, which includes a fixed and a movable plate that interact and define the cavity of the form. The loading sleeve can be arranged horizontally, vertically or with an inclination between horizontal and vertical. The loading sleeve is connected to the pouring spout of the mold and includes an opening at the top of the sleeve, through which the molten metal is poured.

The plunger is positioned so that it moves in the sleeve and forces the molten metal in the sleeve to move into the mold. In a "cold type" machine, the loading sleeve is arranged horizontally and is not heated. Pouring is usually carried out in atmospheric conditions, that is, the equipment is not placed in a chemically inert environment, such as a vacuum chamber. 65 The disadvantages of such machines are discussed in US Pat. No. 3,646,990, particularly in connection with the impossibility of using such machines for casting materials with higher melting points (Tt greater than approximately 10937 (2000"P)), such as superalloys based on nickel, cobalt and iron. In conventional machines with a cold chamber in the charging sleeve, the air is not pumped out, and the plunger compresses the air into the mold as well, causing the injection molded parts to have undesirable and unacceptable porosity. Therefore, in order to prevent air bubbles from being forced in with the with the molten material, the charging sleeve should be filled as much as possible or tilted so that some air, some of which is in the molten material, escapes the mold before injection.

Also, since the charging sleeve is not heated, a surface film or "shell" of molten metal solidifies on the inner surface of the charging sleeve, and in order for the plunger to be able to move through the sleeve to force the molten metal into the mold, the plunger must scrape the film off the sleeves and "destroy the shell". However, if the shell forms a structurally strong member, for example, in the form of a cylinder supported by a sleeve, the plunger and/or associated structural member for moving the plunger may be damaged or destroyed. If the sleeve deforms due to temperature and does not conform to the shape of the plunger, or if the plunger deforms and does not conform to the shape of the sleeve, then metal 7/5 May seep between the plunger and the sleeve ("kickback") and/or some trapped gas may pass between plunger and sleeve, while all this has a detrimental effect on the quality of the parts obtained. See also U.S. Patent No. 3,533,464, Ragiapia et al.

Despite considerable effort, conventional "cold chamber" injection molding machines have not been successfully applied to the production of parts composed of refractory materials such as nickel-based 2o superalloys. Recent attempts at injection molding of refractory materials such as superalloys have resulted in failure of die casting machines and poor quality parts, namely impurities, excessive porosity and liquation, and relatively low strength. and poor multi-cycle and low-cycle fatigue performance.

The general purpose of the present invention is to create die-cast parts that consist of refractory materials such as nickel-based superalloys.

Another object of the present invention is to create superalloy parts, cast under pressure, with properties that are i) similar to the corresponding parts obtained by forging.

A more specific purpose of the present invention is to create superalloy parts having strength, durability and fatigue resistance that are similar to the corresponding characteristics of superalloy parts obtained by forging.

Another goal of the present invention is to create such parts that have complex three-dimensional shapes that are difficult and even impossible to forge. with

Another general object of the present invention is to reduce or eliminate any natural liquation in die-cast superalloy parts. at

A more specific purpose of the present invention is heat treatment to reduce or eliminate natural liquation and topologically closely packed phases in IM 718 die-cast parts.

Another object of the present invention is heat treatment, which may also include appropriate hot isostatic pressing parameters to reduce or eliminate any residual porosity.

Based on the following description and illustrative material, those skilled in the art will understand the additional objectives of the present invention. The essence of the invention. According to one aspect of the present invention, a part cast under pressure, consisting of i? a nickel-based superalloy such as IM 718. Such parts preferably at least meet the strength, long-term strength, and low-cracking-rate requirements of the corresponding forged parts, for example, according to AM5 5663 or AM5 5383. Such parts include, for example, the vane and vane directional -I apparatus of the gas turbine engine. The microstructure of each part is similar to the microstructure of the forged material and is characterized by more uniform grains and the fact that the average fine grain size for the cast part is, for example, less than about AZTM Z (AZTM is the American Society for Testing 2) Materials), mainly AZTM 5 or less. The microstructure is mainly further characterized by the absence of slip lines. In the case of rotating parts such as gas turbine engine blades, it is preferred that the average grain size is less than, for example, preferably AZTM 5 or less, more preferably AZTM 6 or less. o According to another aspect of the invention, a method of heat treatment of a die-cast part made of a superalloy having porosity and natural liquation like cast iron is claimed. The method includes heating the part to a temperature of about 982-11217C (1800-2050"P), preferably between 982-10237C (1800-1875) for about 1-24 hours, due to which liquation is reduced. More preferably, the part is subjected to pressure between about 105-154MPa (15-25K8i) during the heating stage, as a result of which the porosity is significantly reduced at the same time.

F) The parts have both yield strength and tensile strength at both room and elevated temperatures, which are similar to the corresponding characteristics of forged parts composed of the same material, and also have similar multi-cycle and low-cycle fatigue characteristics . The advantage of the present invention is that injection molding is significantly less time-consuming to produce a part from ingot to finished part because it avoids the need to make specially fitted material blanks or prepare a ceramic shell for precision casting from molten models, and because casting performed in a single step, unlike multi-step forging or shell preparation operations. In addition, injection molding allows the production of many parts in a single step b5 Pouring. Die casting, in addition, allows you to produce parts with more complex three-dimensional shapes, which, in turn, allows you to get profiles and other parts with more perfect agrodynamic properties, unlike forging. This invention will make it possible to produce parts that use materials and have shapes that are difficult or impossible to forge. In addition, die-cast parts have greater reproducibility compared to forged or die-cast parts and can be produced closer to their final shape with a proper final surface finish, minimizing finishing operations. All this also reduces the cost of production of such parts. Additional advantages will be apparent from the following illustrative material and detailed description.

Brief description of illustrative material

Fig. 1 - illustrates an injection molded part consisting of IM 718 according to the present invention. 70 Fig. 2 is a photomicrograph illustrating the microstructure of a test rod consisting of IM 718, cast under pressure, according to the present invention.

Fig. 3 is a photomicrograph illustrating the microstructure of a profile consisting of IM 718, cast under pressure according to the present invention.

Fig. 4 is a photomicrograph of the profile of Fig. C after hot isostatic pressing of the profile.

Fig. 5 is a photomicrograph illustrating the microstructure of the profile consisting of forged IM 718.

Figures 7 and 7 illustrate the properties of an IM 718 die-cast part in accordance with the present invention and corresponding forged parts.

Fig. 8 and 9 is a schematic representation of a casting machine for casting under pressure, which is used for the production of parts consisting of IM 718.

Fig. 10 is a diagram of the manufacturing process demonstrating the method of casting IM 718 under pressure according to the present invention.

Fig. 11 is a graph illustrating the dependence of the average grain size and the percentage ratio of liquation in a pressure-cast part with IM 718 as a function of heat treatment temperature in accordance with the present invention.

Fig. 12 is a photomicrograph illustrating a microstructure containing natural liquation in a die-cast part from IM 718.

Fig. 13 is a photomicrograph showing reduced liquation after hot isothermal pressing and i) heat treatment according to the present invention.

Detailed description of preferred embodiments of the invention.

Let's turn now to Fig. 1. A die-cast nickel-based superalloy part according to this invention is generally designated 10. In the illustrated embodiment, the part includes a blade 10 consisting of IM 718 and used in a gas turbine engine. The part includes a profile 12, a base 14 and a shank 16. This invention finds wide application in many applications and is not limited to any particular part or application in gas turbine engines. Preferably, die-cast parts for gas turbine engine applications (as opposed to die-cast parts for other applications) have strength, low crack rates, and high endurance limits as specified in AM5 5663 (AM5 is the Aerospace Specifications of materials) (Kem. U, Rybi. Mar. 1997) (for the corresponding forged parts) or АМ5 5383 |Kem. Uh, fish. Arg. 1993) (for the corresponding parts obtained by precision casting from molten models - for the use of lower strength relative to AM5 5663). Specifications of aerospace materials published by ZAE (Society of Automotive Engineers) IPG! oh "

UUagtepaaie, RA, and incorporated herein by reference. As mentioned above, a common nickel-based superalloy used in gas turbine engines is Ipsope! 718 (IM 718), which nominally contains, in weight percent, about 19 St, 3.1 Mo, with about 5.3 (MO I-Ta), 0.9 Ti, 0.6 Ai, 19 Re, and a base. In general, IM 718 contains, in weight percent, about 0.01-0.05 carbon (C), up to about 0.4 manganese (Mp), up to about 0.2 silicon (51), 13-25 chromium (Cg), up to approximately 1.5 cobalt (Co), 2.5-3.5 molybdenum (Mo), 5.0-5.75 (Columbium (MB) z- tantalum (Ta), -I 0.7-1.2 titanium (Ti), 0.3-0.9 aluminum (A), up to about 21 iron (Be), the rest - almost nickel. Even more preferably IM 718 has a composition: about 0.02-0.04 C, up to about . ), 0.75-1.15 (Ti - M Zh-NYA, 0.4-0.7 AIII, up to about 2) 19 Re, the rest - practically Mi and traces of other elements.

In IM 718, it is possible to make modifications to the composition, for example, by increasing the content of Mb in the material to be poured, as well as by increasing the content of other strengthening elements, to improve strength and other characteristics.

We have produced die-cast parts composed of nickel-based superalloys by using a die-casting machine illustrated and described, for example, in U.S. Pat.

MoMo 3,791,440 and 3,810,505, both authored by Stozv. We have also obtained such parts by casting in "cold chamber" injection molding machines, which typically have a charging sleeve that is not (F) heated, and which have been described above and in US Pat. No. 3,791,440. We have consistently used and prefer the use of "cold chamber" machines in connection with this invention, not least because such machines are less expensive, easier to make, and can be renewed as needed for injection molding applications. such refractory materials, and their repair, by necessity, does not require a lot of money.

Briefly, according to the present invention, at least a single load of material is melted so as to minimize contamination that is associated with either the melting device or the reaction of one or more elements of the material. Therefore, the alloy is heated and melted in a chemically inactive, for example, inert or, preferably, in a vacuum environment, preferably maintaining a pressure of less than 10 Ωm, preferably less than 50 Ωm. The alloy is also heated to a controlled, limited superheat, for example, usually 38-93" (100-200"P) above the melting temperature of the alloy and preferably 10-387C (50-100"P) above,

at the same time, it is preferable to use a non-polluting melting device. We prefer to use a non-ceramic melting system, such as an induction melting device with a garnish.

The material should be superheated sufficiently so that it remains molten until it is squished.

Into the mold, but not enough to prevent rapid solidification of the molten material after injection. The molten alloy is then moved into the horizontal loading arm of the machine, which is preferably in a vacuum environment, and the molten material is compressed under pressure into a mold that can be reused. The process of pouring and injecting the molten material should not take more than a few seconds, and the injection should preferably be performed in less than 1. or 2 7/o seconds in an injection molding machine having a charging sleeve that does not heat up.

It should be noted that the parts after pouring can be subjected to thermomechanical processing, if necessary.

In other words, parts can be forged after injection molding, for example, injection molded parts can serve as preforms for use in a forging operation. We prefer that the parts that are die-cast have the most accurate shape so as to minimize the processing of the parts after /5 Pouring, which reduces their cost.

According to the present invention, the parts produced according to the present invention have a microstructure with small grains with a constant average size, especially for cast parts, and slip lines are absent. look

Fig. 2 and 3, which illustrate the microstructure of a die-cast test rod and profile with IM 718, respectively, and Fig. 5, which illustrates the microstructure of a conventional forged profile with IM 718. In Fig. 2, the average grain size corresponds to approximately AZTM 6. In Fig. 5, the average grain size corresponds approximately to AZTM 10.

The parts are characterized by a small average grain size, for example, for non-rotating parts of a gas turbine engine, such as casings and seals, the average grain size corresponds to ATM 3 or less, preferably AZTM 5 or less. For rotating parts such as gas turbine engine blades, the preferred average grain size is smaller, for example preferably AZTM 5 or less, more preferably AZTM 6 or less. The preferred average grain size and the maximum allowable grain size will be determined by the application of the part, for example, it should be considered whether the part will be used in a gas turbine engine and i) not elsewhere, whether it is rotating or non-rotating, or whether it will function in low temperature environments or with high temperature. Such parts are similar in their properties, preferably at least equivalent to the corresponding parts made of forged material. о о о As a result of examination of die-cast parts, such as those consisting of IM 718, the presence of at least some Laves phases and other topologically close packing phases, as well as natural o liquation, was unexpectedly revealed. The presence of such defects is surprising, given the relatively high speed (compared to precision casting with molten models) at which the molten material cools after injection into the mold.

As discussed earlier, the presence of these defects adversely affects the mechanical properties of parts. at

Depending on the purpose of the parts, these defects should be reduced or avoided. Examples of heat treatment to reduce or eliminate these defects are discussed in relation to Figures 12-14.

As noted above, this invention provides die-cast parts that not only have adequate strength, but also other properties that are similar to or better than those of the corresponding forged parts, such as low cracking rates and high durability. Samples of die-cast "40. ІМ 718 according to this invention were tested to determine the yield strength and tensile strength, as well as plasticity and impact strength. Regarding the tensile strength, the samples of die-cast parts with IM . 718 was tested both at room temperature (approximately 70°C) and at elevated temperatures, such as approximately 6507C (1200"P) which was maintained for some period of time prior to the test. The samples were stretched at a strain rate between 0.076-0.178 mm/mm/min or 0.003-0.007 in/in/min past the yield point, and then the rate was increased to rupture after approximately 1 minute. As shown in Figures 6b and 7, room temperature and elevated temperature injection molded parts are similar in yield strength (0.290), tensile strength, elongation at break, and impact toughness. 2) More specifically, in the case of vanes and guide vanes, such as rotating parts, the die-cast parts are required to have at least strength and impact toughness equivalent to those exhibited by the corresponding forged parts. Vanes, guide vanes and rotating parts consisting of IM 718 must have a conventional yield strength at room temperature of at least 1 GPa (140k5i) and preferably at least 1.05 GPa (150k5i) and most preferably at least 1, 12GPa (160Kz5i), and yield strength at 6507C (1200"P), at least 805MPa (115Kzi), and preferably 875MPa (125Kzi), and most preferably, at least 945MPa (135K5i). Such parts have a tensile strength of at room temperature, at least 1.23GPa (175K5i), preferably, at least 1.3GPa (185K5i) and most preferably,

Ф) at least 1.37GPa (195K5i), and the ultimate tensile strength at 6507С (1200"Р), at least 1GPa (140Kv5i), and preferably 1.05GPa (150Kvi), and most preferably, at least 1.12GPa (160 kV).

In addition, tests were carried out on the long-term strength of a standard set of smooth samples and samples with a notch (containing the material obtained according to the present invention), for example, which correspond to AZTM E292.

The specimens were maintained at a temperature of approximately 6507 (1200°F) and subjected to continuous loading after generating an initial axial stress between approximately 735-770MPa (105-110K5i). In the case of the vane and guide vane material, the specimens ruptured only after at least 23 hours. These values are similar to those found in AM5 5663 above. 65 Long-term strength tests were also performed on approximately 7047 (1300) of a similar standard set of smooth and notched specimens (containing material obtained under this invention),

for example, which correspond to AZIM E292. The specimens were subjected to continuous loading after generating an initial axial stress between approximately 420-455 MPa (60-65 Kzi). In the case of the vane and guide vane material, the samples did not rupture until at least 40 hours later.

They also determined creep properties at approximately 6507C (12007). The samples were maintained at a temperature of about 6507 (12007) and loaded to obtain an axial stress of at least about 560 MPa (80 Kvi). It was determined that the time to 0.196 plastic deformation in the case of material for vanes and guide vanes exceeds approximately 15 hours. | again, the specific values required will vary depending on the particular purpose for which the parts are being manufactured. 70 For non-rotating parts such as casings, flanges and seals such as rings, the above values exaggerate the required values. More specifically, non-rotating parts such as rings and seals made of IM 718 should have a conventional yield strength at room temperature of at least 910MPa (30Kzi), and preferably at least 1GPa (140Kzi), and most preferably, at least 1.05GPa (150K5i), and a yield strength at 6507C (1200) that is at least 735MPa (105K5i), and preferably at least 805MPa (115K5i), and most preferably at least 875MPa (125K5i). Such parts have a tensile strength at room temperature of at least 1.16GPa (165K5i), and preferably at least 1.23GPa (175K5i), and most preferably at least 1.3GPa (185Kv5i), and a limit tensile strength at 6507 (12007), which is at least 875MPa (125K5i), and preferably at least 945MPa (135kKz5i), and most preferably at least 1.02GPa (145Kz8i).

In addition, tests were carried out on the long-term strength of a standard set of smooth samples and samples with a cut (containing the material obtained according to the present invention), for example, which correspond to AZTM E292.

The specimens were maintained at a temperature of approximately 6507 (1200°F) and subjected to continuous loading after generating an initial axial stress between approximately 735-770MPa (105-110K5i). In the case of the vane and guide vane material, the specimens ruptured only after at least 23 hours, and the relative elongation was at least about 695.

Long-term strength tests were also performed on approximately 7,047 (1,300) similar standard i) sets of smooth and notched specimens (containing material obtained according to the present invention), for example, conforming to AZIM E292. The specimens were subjected to continuous loading after generating an initial axial stress between approximately 420-455 MPa (60-65 Kzi). In the case of the material for the rotor blades and guide vanes, the samples did not rupture until at least 85 hours later.

They also determined creep properties at approximately 6507C (12007). The samples were maintained at a temperature of about 6507 (12007) and loaded to obtain an axial stress of at least about 560 MPa (80 Kvi). It was determined that the time to 0.196 plastic deformation in the case of material for vanes and guide vanes exceeds approximately 15 hours. | again, specific ones are needed

The values will be different depending on the specific purpose for which the parts are manufactured. uh-

AM5 5663 provides the following properties:

Property Room temperature 1200 "Р (6507С) /-10

Tensile strength, minimum 1.26GPa (180Kv5i) 1GPa (140k5i) «

Yield strength, mm s 0.295 strain, minimum 1.05GPa (150k5i) 875MPa (125K85i)

Relative elongation in 40, minimum 1095 1095 :z» Reduction of area, minimum 1290 1290

АМ5 5383 provides the following properties: i Property Room temperature («v | Tensile strength, minimum 840MPa (120Okz85i) syu Yield strength, W 0.295 deformation, minimum 735MPa (105k5i) (ав) 50 Relative elongation in 40, minimum Зо o Decrease in area , minimum 890

As stated in AM5 5663, the properties for forged material differ depending on whether the specimens are tested in the longitudinal or transverse direction, for example, the properties are not isotropic and the lower 22 values are obtained in the transverse test.

GF) In addition, long-term strength tests were carried out on a standard set of smooth and notched samples (containing the material obtained according to the present invention), for example, which correspond to AZTM E292.

The specimens were held at a temperature of approximately 6507 (1200"E) and subjected to continuous loading after generating an initial axial stress between approximately 735-770MPa (105-110Kvi). The specimens ruptured 60 after at least 23 hours. These values are consistent with the requirements of AM5 5663.

For parts with lower strength, namely those that meet the requirements of АМ5 5383, long-term strength tests were carried out on a standard set of smooth and notched samples. The samples were maintained at a temperature of 7047 (1300) and subjected to continuous loading after generating an initial axial stress of approximately 462MPa (65K5vi). Samples should break only after at least 23 hours.

Turning now to Figures 8, 10 and 10, nickel-based superalloys such as IM 718 should preferably be melted and cast in a chemically inactive environment, such as in the presence of an inert gas, or preferably in a vacuum environment. The preferred method of casting parts under pressure is described in the application "Method

Manufacture of Die Cast Parts of Refractory or Reactive Materials" and in the co-pending application "Apparatus for Die Casting of Refractory Materials" filed on the same date as this application and which are incorporated herein by reference in their entirety Preferably, a single charge or small batch (less than about 4.5 kg (10 lb)) of material is prepared (Figure 10, step 44). the horizontal loading sleeve of a cold-chamber die-casting machine, from which air should preferably also be bled so as to partially fill the sleeve.

First, the material to be cast under pressure is melted (Fig. 10, step 4 b) in the device 18, which is shown in Fig. 8 and 9. If reactive materials are to be cast, such as superalloys containing chemically active elements , it is important to melt the materials in a chemically inert environment in order to prevent any reaction, contamination, or other condition that could adversely affect the quality of the resulting parts.

Because some gases can be entrained by the molten material at the melt point and cause excessive porosity in the die-cast parts, we prefer to melt the material in a vacuum environment as opposed to an inert environment such as argon. Preferably, the material 20 melts in the melting chamber 20, which is connected to the vacuum source 22, so that the chamber is at a pressure of less than 10 Ωm, and preferably less than 5 Ωm.

We prefer to melt nickel-based superalloys such as IM 718 by induction remelting or Garnish Melting (IZK) 24, for example using a crucible produced by Sopsags

Sogrogayop oi Kapsosavs, M) which is capable of rapidly and cleanly melting a single load of material to be cast, for example, up to about 25 pounds of material. In induction remelting with garnish, the material melts in a crucible that has numerous metal (usually copper) fingers that are fixed next to each other. The crucible i) is surrounded by an induction coil connected to a current source 26. The fingers have passages for circulating cooling water to and from the water source (not shown) to prevent melting of the fingers. The field generated by the coil passes through the crucible and heats and melts the material in the crucible. The suzo field also serves to stir and agitate the molten metal. A thin layer of material solidifies on the wall of the crucible and forms a garnish, because of this, the ability of the molten material to lead to corrosion of the crucible is reduced. Due to the proper selection of the crucible and coil and the level of power and frequency applied to the c coil, it is possible to force the molten material out of the crucible by the levitation effect of the molten material. at

Since some time will necessarily elapse between the melting of the material and the injection of the molten material into the mold, the material is melted with a limited superheat - high enough that the material remains at least substantially molten until it is injected, but low enough that so that rapid solidification occurs after injection, for example, so that small grains can form. For superalloys, we prefer to limit the superheat to about 937 (200"P) above the melting point, preferably less than 387C (100"P), more preferably less than 107 (50). Although we prefer to melt single loads of material using an induction remelting device with a garnish, the material can be melted in other ways, ;" such as vacuum induction melting (VIM), electron beam melting, current or plasma arc melting. In addition, we do not exclude the melting of a large volume of material, for example, several loads of material together in a vacuum environment, with the subsequent movement of single loads of molten material into the loading sleeve for injection into the mold. However, since the material melts in a vacuum, any equipment used to move the molten material must normally withstand high temperatures and be located in a vacuum chamber, and in turn, the chamber must be relatively large. Additional equipment requires additional funds, and a large 5or vacuum chamber accordingly requires more time to pump out air, which increases the duration of the entire production process. o In order to move the molten material from the crucible to the loading sleeve 30 of the machine (Fig. 10o, step 48), the crucible is mounted in such a way as to make a translational movement (arrow 32 in Fig. 9) and also a rotary movement (arrow 33 in Fig. 8) around the pouring axis (not shown), and, in turn, is attached to a motor (also not shown) for rotating the crucible to pour the molten material from the crucible through the inlet 35 of the loading sleeve 30 with or without a pouring funnel or bowl, which joins the sleeve. Progressive

F) movement is carried out between the melting chamber 20, in which the material is melted, and the position in a separate vacuum chamber 34, in which the loading sleeve is located. The casting chamber 34 is also provided with a chemically inactive medium, preferably a vacuum medium under a pressure of less than 100 µm, and preferably less than 50 µm. The melting chamber 20 and the casting chamber 34 are separated by a vacuum valve or other suitable means (not shown) in order to minimize the loss of vacuum in the event that one chamber becomes accessible to the atmosphere, for example, to have access to some assembly in a particular camera

As noted above, the molten material is transferred from the crucible 24 to the loading sleeve ZO through 65 the inlet 35. The loading sleeve 30 is connected to a multi-section mold 36, which can be used repeatedly and which defines the cavity 38 of the mold. Sufficient molten material is poured into the loading sleeve to fill the mold cavity, which may include one or more parts. We have successfully cast 12 parts in one go, for example, using a 12-cavity mold.

The depicted mold 36 includes two parts Zba and Z6B, which interact and define a cavity 38 of the mold, for example, in the form of a profile for a compressor of a gas turbine engine. The mold 36 is also connected to a vacuum source to allow air to be pumped out of the mold prior to injecting the molten material, and may also be surrounded by a separate vacuum chamber. One part of the Zba or 3665 mold is fixed, but the other part is movable relative to the first part, for example, by means of a hydraulic assembly (not shown).

The molds preferably include ejectors (not shown) to facilitate ejection of the solidified material from the mold.

The mold can be made of a variety of materials and must have good specific thermal conductivity and be relatively resistant to erosion and chemical corrosion resulting from injection of the molten material.

An exhaustive list of possible materials would be quite large and would include materials such as metals, various ceramics, graphite, and metal matrix composite materials. For mold materials, we have successfully used tool steel such as NI1Z and U57, molybdenum and tungsten-based materials such as

TAM and Apmiisu, copper-based materials such as high-hardness copper-beryllium alloy "Moidtach", cobalt-based alloys such as E75 and I 605, nickel-based alloys such as IM 100 and Kepe 95, iron-based superalloys and mild carbon steel such as 1018. The choice of mold material is a critical factor in cost-effective part production and depends on the complexity and quantity of parts to be cast, as well as the current cost of producing the part.

Each form material has properties that make it possible to use it in different cases. For inexpensive mold materials, mild carbon steel and copper and beryllium alloys are preferred due to the fact that they are relatively easy to machine and form easily. Refractory metal, such as tungsten and molybdenum-based materials, are preferred for more expensive, bulkier parts due to their good strength at high temperatures. Cobalt-based alloys and nickel-based alloys and more highly alloyed tool steels provide a compromise between these two groups of i) materials. Coatings and surface treatments can be applied to improve the operational properties of the device and the quality of the resulting parts. The mold may also be connected to a coolant source such as water or a heat source such as oil (not shown) to provide the mold with the required temperature during operation. Additionally, mold lubricant can be applied to one or more selected parts of the mold and the injection molding machine. The grease used should generally increase the quality of the cast parts and, more specifically, it should be resistant to thermal destruction, so as not to contaminate the material being crushed.

The molten metal is then moved from the crucible to the loading sleeve. Sufficient o c5 of molten metal is poured into the charging sleeve to fill the pressure cavity and associated spigots, the mold itself, and other cavities. Since IM 718 does not create a "shell" like titanium alloys, it is possible to fill the loading sleeve. However, we produced high-quality castings where the sleeve only filled less than 5095, less than about 4095, and less than about 30965.

An injection device, such as a plunger 40, acts in conjunction with a loading sleeve 30, and hydraulics or other suitable assembly (not shown) moves the plunger in the direction of arrow 42 to cause the plunger to move c between the position shown in solid lines and the position which is depicted by dashed lines, as a result of which . it will crush the molten material from the sleeve ZO to the cavity 38 of the mold (Fig. 10, step 50). In position, huh?" which is shown in solid lines, the plunger and sleeve together define a volume that is substantially greater than the volume of molten material to be crimped. Preferably, the volume should at least double the volume of the material to be crushed, more preferably at least three times. Therefore, the volume of molten -I material moves from the crucible to the sleeve, if the sleeve is only partially filled, some material or film solidifying on the sleeve forms only a partial cylinder, for example, an open arcuate surface, and it is more easily scraped off or destroyed during injection of metal and again enters the molten 2) material. For injection, we used a plunger speed between about 0.77m/s (Collection (inches per 5o backend)) and 7.7m/s (ZOOirv), and now we prefer a plunger speed between about 1.3- 4.5 m/s (50-175 irv). The plunger normally moves when the pressure is at least 8.4 MPa (120 psi), and preferably at least 10.5 MPa (1500 psi). As the plunger approaches the end of its stroke, when the mold cavity is filled, it begins to transmit metal pressure. The pressure imparted to the metal is then increased, preferably to at least 3.5 MPa (50 Orgi) and more preferably to at least about 10.5 MPa (150 Orgi) in order to completely fill the mold cavity. The pressure is also increased to minimize porosity and to reduce or prevent any shrinkage of the material during

F) cooling. After a sufficient period of time required for the material to solidify in the mold, ejectors (not shown) are activated to push the parts out of the mold (Figure 10, step 52).

It is known from the prior art that cast parts, in general, and die-cast parts, in particular, tend to have some porosity, generally up to several percent. Accordingly, and especially if such parts are used in cases with increased requirements, namely in compressor profiles for gas turbine engines, there is a need to reduce and preferably eliminate porosity, for which they are processed, if necessary (Fig. 10, step 54). The parts are then subjected to hot isostatic pressing as described above to reduce and substantially eliminate any porosity in the cast parts. For nickel-based superalloys such as IM 65 718, we prefer hot isostatic pressing at a temperature between about 982-10937C (1800-2000"F), more preferably between about 982-1023"C (1800-1875"F) for a minimum of approximately 4 hours and at a pressure between approximately 105-175MPa (15-25Ksi).

If necessary, each part can then be subjected to heat treatment. For profiles consisting of die-cast IM 718, the heat treatment includes a standard and commercially acceptable treatment such as that described in AM5 5663.

Actual heat treatment and hot isostatic pressing parameters may vary depending on the required properties of the part, its application, and the predetermined cycle time for the process, but the temperature, pressure, and time applied during hot isostatic pressing should be sufficient to practically destroy all porosity and homogenize any remaining cast liquation, 7/0 however, they should not cause significant grain growth.

The parts are inspected (Fig. 10, step 56) using conventional methods of inspection, for example, by fluorescent penetrative defectoscopy (EPI), radiographic defectoscopy, visual inspection, and after carrying out the inspection they can be used, or, if necessary, processed further or re-processed (Fig. 10, step 58).

Let's pay attention to heat treatment. We have determined that liquation and topologically close-packed phases can be reduced or virtually eliminated at substantially reduced temperatures compared to previous parts, and therefore the presence of native liquation can be avoided within parameters such as hot isostatic pressing. Heat treatment involves heating the material to a temperature between about 982-11217C (1800-2050) for a period of between about 1-24 hours and at a pressure of about 20.105-175MPa (15-25Kv8i), whereby the porosity must be destroyed. Processing is preferably carried out in an inert environment, such as argon. Actual parameters may vary depending on the desired application of the part and the predetermined cycle time for the process, but the temperature, pressure, and time should be sufficient to virtually eliminate all porosity and reduce liquation in the cast part (illustrated in Figure 12), but they are not should cause significant grain growth. Fig. 13 illustrates a die-cast IM 718 material after being heated to a temperature of approximately 10107 (18507) for 2 hours without pressure in order to demonstrate the reduction of liquation. Applying the appropriate pressure during isostatic heating during i) this period destroys the existing porosity.

Temperature and time will affect the resulting grain size of the part. On the example and with reference to

Fig. 11, an injection-molded IM 718 part has an average grain size of approximately А5TM 9 and a percent liquefaction ratio of approximately 3095 (see figure to the left of the curve). The samples were heated at temperatures between about 954-11217C (1750-2050°F) and the machined parts had reduced crystallization and average grain sizes that increased with increasing temperature. Average grain size growth increased with increasing time, especially at elevated temperatures. The curve shown in Fig. 11 corresponds to die-cast IM 718, but other materials may exhibit similar behavior. See, for example, the pending application "Diecast Superalloy Parts".

As a result of our work with nickel-based superalloys, we believe that several conditions are important for the production of good quality castings. Melting, pouring and injection of material, especially for reactive materials, should be carried out in a chemically inert environment, and we prefer to carry out these operations in a vacuum environment, in which the pressure is maintained preferably less than 10Om, and more preferably "

Less than z0Ωm. The superheat must be sufficient so that the material remains substantially and completely molten from the time it is poured until it is injected, but also so that it can cool rapidly and form small grains after injection. Due to relatively low overheating, displacement and injection;" of molten material must be fast enough to be carried out before the metal solidifies.

It turns out that the obtained microstructure, such as the grain size, corresponds to the transverse thickness of the part, which

The casting, as well as the mold materials used and the superheat used, namely thinner -I sections tend to include finer grains and thicker sections (especially the inner parts of thicker sections) tend to include larger grains. The higher the specific thermal conductivity of the mold materials, the finer the grains of the parts due to the effect of lower overheating. We believe this is due to the relative 2) cooling rates of these sections. The speed at which the plunger moves and, consequently, the rate at which the material is forced into the mold appears to affect the final surface of the cast part, although the design of the mold system as well as the material of the mold in combination with the speed of injection can play a role in this participation. Careful control of post-casting heat treatment is necessary to fully realize the advantages offered by the relatively fine microstructure of an injection-molded casting.

Die casting also has other significant advantages over forging. The time required to produce a part from ingot to final part is greatly reduced by eliminating the need to prepare specially fitted material blanks and by casting in a single

F) stage, in contrast to numerous forging operations. With injection molding, numerous parts can be produced in a single injection. Injection molding allows the production of parts with more complex three-dimensional shapes, which allows the introduction and application of new design and manufacturing software technology in industries such as gas turbine engines, and the production of more efficient profiles and other parts. We believe that injection molding will allow the production of parts with complex shapes, while using materials that are difficult or impossible to forge into these shapes. In addition, die-cast parts have greater reproducibility than parts obtained by forging or precision casting from molten models, and their shape can be closer to the final shape and the final surface can be of a higher quality, which allows 65 to minimize operations proofing after pouring, which also reduces the cost of producing such parts.

Heat treatment according to the present invention provides certain advantages. This heat treatment eliminates casting defects, such as porosity, Laves liquation, and other undesirable topologically closely packed phases, but ensures the formation of small grains, which gives the parts excellent mechanical properties. In addition, this treatment allows to eliminate all the above-mentioned harmful effects in a single step that saves money, time and effort.

Despite the fact that this invention has been described in detail above, numerous options and substitutions are possible that do not contradict the spirit of the invention or the scope of the following claims. Therefore, it should be understood that the invention has been described for purposes of illustration and not limitation. 70, M

Fig. 1 12 14

ShK that 16

In ra in "Zh. that school

J

And what's more. | still i I ' in with tt. ny Ya y Ky o - SHY - "- y cho Fig. 2 o o Dt -iiik so a E. yiv g adm " tsi o

I'm going there, yeah, Gee-

Fe V. with zay o

KO has and is. And y - y p- she an o NOT " y: we I : - s 2" I o. . «lu iizk: g Ku U veto; 15th, svi M ony ikh -I y ' ach y nyh PD from U 7

V. ikh Ch dis b da M o vooyaiya EK alu chu ЖЖ poly Kun nya s u what Ve ; Gak IM k show Shchi - Kk zn UA. LK t: y o Fig. 3 mak esh and MNK and Ky o ol Bona Pk. pi o a CHI ! 7 I know that I. in Por I lo kl s v kora - I will return ACTS A "7 fe" o Mk UZH" di My i, o

F) aa so A A o in PA u

Ky ky tov korve b, KE Y I z u "ZHE GE: and for "ELE "boru VL sh: mak tia and y .

I put o GuUZHKI, zla ku ik ze Ada YOU M a niy bo KVU ev ch nyrmyu, b5

; | ho m 55 pe v i ME popy or A KK

Fig4 oh oh

YIV p

КС Ку у а Куй я их ФЯ, о кл ге о пк Х у я чеКоса sk - I и VO chandelier в КА dna; MU Fig. 5, y i l ' o g - h s - BM o

I eat and drink in the minutes of ia de kova Sh o r M KA r t iz o h From Her; ho and elk and grove Z, and all zv z OK, and i- - 220 yu and 200 Yad 3 RZHA 1085 - s 100 shi --- RZHA 1010. tiy . And day - pzhnzhtzhtTtTtldmyazhnntntynsh and bi A 2 same 54-A - --

V. I : 160 y: No sh -- o ny dy she SHY Y

F YAN sho sho z yuoi i SHHI SHHI SHHI I o CT 5 kt OT5' 850 5850 1571200 u5'1200 5

OIE SAB5T 718 - drink ice under pressure in Lithuania from Ipsope! 718 of them) CT U5 - yield strength at room temperature; AND

KT ЦТ5 - tensile strength limit at room temperature; 850 5 - yield strength at 850E; 60,850 units - breaking strength limit at 850E; 1200 UZ - yield strength at T200E; 1200 05 - breaking strength limit at 1200E. b5

ЕЕ РМА 1085 g ж пи: то п ; SHYH TK PE

B 15 p Y 5 8.o 5: KYA 5 Z 5 yu

Eya De NE KO BO SOYA o-B-AZT ES A-tyat IMRASTI-850 EI -t850 IMRAST-1200. EC

OPIE SABZT 718 - die cast from Ipsope! 718

CT EG. - elongation at room temperature; | high school

CT track - impact viscosity at room temperature; 25,850 E:. - elongation at 850E; i) 850 iprasi - impact viscosity at 850E; 1200! - elongation at 1200E.D o "Fig. 8 18 x 29 o 36 o 3 s) o

And also I and from 40. | ЗВ « and is ДЯ | | schi s 40 42 khz» Zva ZbB -I o o 2 87 34 ms,

Gi) zv «| And I'm going to do something about it zvB bo and C and Salvation 26 24 32 !

Fig. 9 5 bo

Fig. 10

Preparation of loading material: 46

Melting of a single loading of material in a vacuum with limited overheating 48 that Infusion of molten material into a partially filled loading sleeve sch , 50 (8)

Injection of the molten material into a form that can be used repeatedly at 52 so o : m

Pushing out the part

FOR " - -

Processing after casting, for example, by hot isostatic. pressing, chemical proofing "» proofing in environments, etc.

Repetition or application

F) t 60 b5

Fig. 11

Die cast from INSOMEA. 718 Sep 19 40 Sun)

Ф тю ХО З 8 th-

E 20 (pl

HER h F 7 s at 10 f

Жо - 5 5 6 З ш гу d) и о о ни и з хе», e stalu ba U s 17506 1VOOR 1850 1900 0950 2000 2О5О i9)

Temperature "c) py ter i dum prog KN rek eV in A NI o

KY KN i i MK, um KE ikh arch, Dy . gy MK rya zheny "and o

b schu; v ry Kun aty rt pi mu KM i yun U sie o ly AK o i zhi a she zv KO o MK Ve UMO UA im n se ot De. in the Academy of Sciences of; ii Ada: My grandmother

Ж you ab fs uchi you і вт т vulyat I sht ED

And AK

Yason nyk sho EN Kr ri ti MN LYA

In a pi don a in ZY KK

Pd VO | Ou Ky U « hu U Z oo UMA i and Kim Zo o nNi with 40 u pet GL, . Gu zu. and I; zi noyakh seyn afk ih spena, Myty zhu, in DN m vu yanku:

ON och mo i na la - . "from ; Te U Yad OO Fig. 12

In the CC of the AN s is Ya vv ru " " Still pe o VE mele

PO ZHE NI au, IN a and E. still KO Z MALYUKI

GRETS SD om od ZK Y

Kor o ukh i DN i pud ukh - VYN mae vini m AD EV OK AKya OA duka

U Do A ku u Ai u z EY o RON o krai Ky SHE

TKA o A --k o o i NAV M rt ru oyu KEDI NAME sonia ney s !

F) name) 6o 65

Who and where are you?

SL o VK VN oh ay sa yak SYU Kh ry 8 KU s y

Same me so p KK

A snagy, A usouta a As M t VK se o o, you AVK, their kl which, i

R "Bery t zi Kk ryavky va ke RYN pr, teka fs Yan Kr i Kn t se nn Ne o ry o i NNYA

Tan ms Sho s, still j i i van NN SHE uk mn v pak ko ny an nn ny I i KA I ves yuЬM ro em ОН A

M You are not in, ee so ni ke pol shi in Mai m - o;

And from the day of them en YN sor all VV se ide a VC

Ku u VO hu ef KK

ME SEN Os ke i i tiki aa i

Ku o ek ik

EK vd M is . yu viku nn 0 PHYS

You are a rivulet

Java ZhK pike is higher

I am a protector of my heart.

ECO I KA AL and the court of the senate id onco. how are you 6)

Claims (5)

The formula of the invention 1. The method of manufacturing gas turbine engine parts, in which a nickel-based superalloy material is melted, a gas turbine engine part is poured from it, and the resulting part is subjected to hot isostatic pressing for at least 4 hours, which is characterized by the fact that before pouring the part, the superalloy material, which has composition, weight 95: carbon 0.02 - 0.04, chromium 17 - 21, molybdenum together with tungsten /-:F and rhenium 2.8 - 3.3, niobium together with tantalum 5.15 - 5.5, titanium together with vanadium and hafnium 0.75 - 1.15, about aluminum 0.4 - 0.7, iron up to 19, manganese arbitrarily up to 0.35, silicon up to 0.15, cobalt up to 1, and the rest - nickel, overheat above the melting point at less than 93 "С, casting of the part is carried out by pouring under - pressure, and hot isostatic pressing of the obtained part is carried out at a temperature of 982 - 1023 "С and a pressure of 105 - 175 MPa, ensuring at the same time the production of a practically non-porous material of the part, the value of liquation is not more than 4095 and the average grain size according to AZTM Z or smaller. " 2. The method according to claim 1, which is characterized by the fact that the superalloy material is superheated above the melting point by less than 3870. c C. The method according to claim 1 or claim 2, which differs in that the superalloy material is melted, overheated and "» poured under pressure in a vacuum environment. " 4. The method according to any one of claims 1, 2 or 3, characterized in that the superalloy material is melted and superheated in an induction melting furnace with a garnish. 5. A part of a gas turbine engine, cast under pressure, which consists of a nickel-based superalloy, which - differs in that the superalloy has a composition, wt. 90: carbon 0.02 - 0.04, chromium 17 - 21, molybdenum together with tungsten and rhenium 2.8 - 3.3, niobium together with tantalum 5.15 - 5.5, titanium together with vanadium and hafnium 0 .75 - 1.15, aluminum 0.4 - 0.7, iron up to 19, arbitrarily manganese up to 0.35, silicon up to 0.15, cobalt up to 1, and the rest - about nickel, while the material of the part is practically non-porous and has a liquation value of no more than 4095 and 20 the average grain size according to AZTM Z or smaller. m) Official Bulletin "Industrial Property". Book 1 "Inventions, useful models, topographies of integrated microcircuits", 2004, M 10, 15.10.2004. State Department of Intellectual Property of the Ministry of Education and Science of Ukraine. F) name) 60 b5