High-performance GH4169G high-temperature alloy bar as well as preparation method and application thereof

Abstract

The invention belongs to the field of nickel-based wrought superalloy hot working, and particularly relates to a high-performance GH4169G superalloy bar and a preparation method and application thereof.The method comprises the steps that 1, a target cast ingot is prepared, specifically, the GH4169G alloy cast ingot prepared through a set technology is selected and subjected to homogenization treatment and machining treatment in sequence, and the target cast ingot with the height-diameter ratio being 2.0-3.0 is obtained; 2, cogging and forging, wherein the target cast ingot is subjected to 4-6 heating number radial and axial deformation treatment, and a bar billet is obtained; and 3, finished product forging is conducted, specifically, the bar blank is subjected to radial deformation treatment of 3-5 heating numbers, and a target bar is obtained. The bar prepared by the method can be kept without cracking or breaking for at least 35 hours when being loaded with stress of 690 MPa in an environment of 680 DEG C, and can be applied to the preparation process of aviation parts.

Description

Technical Field

[0001] The invention belongs to the field of hot processing of nickel-based deformed high-temperature alloys, and specifically relates to a high-performance GH4169G high-temperature alloy bar and a preparation method and application thereof. Background Art

[0002] GH4169G alloy is an advanced nickel-based high-temperature alloy material independently developed in China. It is developed on the basis of high-quality GH4169 alloy by adopting the method of P and B micro-alloy composite strengthening. While maintaining the excellent performance of GH4169 alloy, GH4169G alloy increases its use temperature from 650℃ to 680℃, and does not reduce the mechanical properties and process properties of GH4169G alloy at 680℃.

[0003] At present, GH4169G alloy has achieved initial results in the initial development stage, but has not yet been applied to aviation rotating parts. The main difficulty is that although the increase in the content of P and B elements in the alloy has achieved performance enhancement, the increase in the ingot size (Φ508mm) in industrial production has aggravated the segregation of GH4169G alloy, which is easy to cause cracking of bars and poor durability during the actual forging process. The existing domestic bar forging processing technology is not mature enough, resulting in the inability to mass produce and apply GH4169G alloy bars.

[0004] In view of this, the inventor provides a high-performance GH4169G high-temperature alloy rod and a preparation method and application thereof to solve the above-mentioned technical problems. Summary of the invention

[0005] The purpose of the present invention is to overcome the shortcomings of the above-mentioned prior art and to provide a high-performance GH4169G high-temperature alloy rod and a preparation method and application thereof. The method can prepare a GH4169G high-temperature alloy rod with uniform structure by adopting a set deformation mode and process parameters.

[0006] In order to achieve the above object, the present invention adopts the following technical solutions:

[0007] In one aspect, the present invention provides a method for preparing a high-performance GH4169G high-temperature alloy bar, comprising the following steps:

[0008] Step 1, preparing a target ingot: selecting a GH4169G alloy ingot prepared by a set process, and sequentially performing homogenization treatment and machining treatment on the ingot to obtain a target ingot with a height-to-diameter ratio of 2.0 to 3.0;

[0009] Step 2, blank forging: subjecting the target ingot to 4 to 6 rounds of radial and axial deformation treatment to obtain a blank;

[0010] Step 3, finished product forging: subjecting the bar blank to 3 to 5 rounds of radial deformation treatment to obtain a target bar.

[0011] It should be noted that the target ingot has a height-to-diameter ratio of 2.0 to 3.0, which is suitable for subsequent billet forging. If the height-to-diameter ratio is too large, it is easy to cause breakage during the subsequent forging process, while if the height-to-diameter ratio is too small, it is not conducive to radial deformation of the material.

[0012] Furthermore, in step 1, the GH4169G alloy ingot is produced by a triple smelting process of VIM+ESR+VAR (vacuum induction melting+electroslag remelting+vacuum consumable remelting ingot).

[0013] Furthermore, in step 1, the process of homogenizing the GH4169G alloy ingot in a high-temperature furnace is as follows: the cold material is charged into the furnace and heated to 1100°C-1130°C at a heating rate of 80°C / h-100°C / h, kept warm for 40h-50h, then heated to 1160°C-1190°C at a heating rate of 2°C / h-5°C / h, kept warm for 80h-100h, and finally cooled to 500°C-850°C in the furnace and then air-cooled to room temperature.

[0014] Furthermore, in step 2, in the radial-axial deformation treatment of 4 to 6 times, the treatment method and parameter value range of each time are the same;

[0015] The radial-axial deformation process of the first fire is as follows: heating the target ingot to 1020°C to 1080°C, holding the ingot for a time greater than or equal to 0.6D, and then deforming the ingot by upsetting first and then drawing. During the deformation process, the deformation reduction rate is 30mm / s to 80mm / s to obtain an intermediate billet, and finally the intermediate billet is subjected to the radial-axial deformation process of the next fire;

[0016] Wherein, D is the diameter of the bar before the current forging fire, and the diameter of the bar in the first fire of the open forging is the diameter of the target ingot.

[0017] Specifically, the columnar dendrite structure in the target ingot can be fully broken up through 4 to 6 fire deformations, providing an excellent bar blank for finished product forging.

[0018] The above-mentioned holding time is obtained based on the thermal conductivity of the high-temperature alloy and actual engineering applications. The holding time can ensure that the target ingot is fully heated through.

[0019] The above deformation reduction rate is beneficial to breaking the columnar dendrites in the target ingot.

[0020] Furthermore, during the upsetting process, the axial deformation is 15% to 25%; during the drawing process, the radial deformation is 20% to 25%.

[0021] Furthermore, in step 3, in the radial deformation treatment of 3 to 5 times, the treatment method and parameter range of each time are the same;

[0022] The radial deformation process of the first fire is as follows: heating the bar blank to 1005°C to 1040°C, holding the bar blank for a time greater than or equal to 0.4D, and then drawing the bar blank. During the drawing process, the deformation reduction rate is 40mm / s to 60mm / s to obtain an intermediate bar. Finally, the intermediate bar blank is subjected to the radial deformation process of the next fire.

[0023] Wherein, D is the diameter of the bar before the current forging, and the diameter of the bar in the first forging of the finished product is the diameter of the bar blank.

[0024] Specifically, the structure of the rod blank can be fully recrystallized through 3 to 5 times of deformation, obtaining an excellent structure to ensure the performance of the material.

[0025] The above-mentioned holding time is obtained based on the thermal conductivity of the high-temperature alloy and actual engineering applications. This holding time can ensure that the billet is fully heated through.

[0026] Furthermore, during the drawing process, the radial deformation is 25% to 45%, thereby ensuring the minimum energy required for the recrystallization of the rod blank.

[0027] On the other hand, the present invention provides a high-performance GH4169G high-temperature alloy bar, which is prepared by the preparation method as described above, and can remain without cracking or breaking for at least 35 hours in an environment of 680°C and loaded with a stress of 690MPa.

[0028] In another aspect, the present invention provides a use of the high-performance GH4169G high-temperature alloy rod as described above in the preparation of aviation parts.

[0029] Compared with the prior art, the present invention has the following beneficial effects:

[0030] The present invention provides a method for preparing a high-performance GH4169G high-temperature alloy bar. In the blanking forging, 4 to 6 fires of deformation are set to fully break the columnar dendrite structure in the target ingot, providing an excellent bar blank for the finished product forging. Further, 3 to 5 fires of deformation are set in the finished product forging to fully recrystallize the structure of the bar blank to ensure the performance of the material. The present invention solves the problems of bar cracking and inability to mass produce during alloy forging. The prepared GH4169G high-temperature alloy bar has uniform overall structure, excellent durability at a high temperature of 680°C, and a life span of more than 35 hours under a loading condition of 690MPa stress. BRIEF DESCRIPTION OF THE DRAWINGS

[0031] The accompanying drawings are incorporated in and constitute a part of this specification and, together with the description, serve to explain the principles of the present invention.

[0032] In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the drawings required for use in the embodiments or the description of the prior art will be briefly introduced below. Obviously, for ordinary technicians in this field, other drawings can be obtained based on these drawings without paying any creative labor.

[0033] Figure 1 This is a flow chart of the preparation method of GH4169G high temperature alloy rod of the present invention;

[0034] Figure 2 This is a high-magnification microstructure diagram of the core of a Φ250 mm rod prepared in Example 1 of the present invention;

[0035] Figure 3 This is a high-magnification microstructure diagram at the R / 2 position of the Φ250 mm rod prepared in Example 1 of the present invention;

[0036] Figure 4 This is a high-magnification microstructure diagram of the edge of the Φ250 mm rod prepared in Example 1 of the present invention. DETAILED DESCRIPTION

[0037] Here, exemplary embodiments will be described in detail, and the embodiments described in the following exemplary embodiments do not represent all embodiments consistent with the present invention. Instead, they are only examples consistent with some aspects of the present invention described in detail in the appended claims.

[0038] Example 1

[0039] On the one hand, this embodiment provides a method for preparing a high-performance GH4169G high-temperature alloy bar, comprising the following steps:

[0040] Step 1, preparing a target ingot: selecting a GH4169G alloy ingot prepared by a VIM+ESR+VAR triple smelting process, and performing homogenization treatment and machining treatment on it in sequence to obtain a target ingot with a height-to-diameter ratio of 2.6;

[0041] Step 2, blank forging: subjecting the target ingot to 4 rounds of radial and axial deformation treatment to obtain a blank;

[0042] Step 3, finished product forging: subjecting the bar blank to radial deformation treatment for three times to obtain a finished round bar with uniform structure and excellent performance.

[0043] Wherein, in step 1, the process of homogenizing the GH4169G alloy ingot in a high-temperature furnace is as follows: the cold material is charged into the furnace and heated to 1100°C at a heating rate of 80°C / h, kept warm for 45h, then heated to 1160°C at a heating rate of 5°C / h, kept warm for 100h, and finally cooled to 500°C and then taken out of the furnace and air-cooled to room temperature;

[0044] Furthermore, the cooled ingot is machined to remove surface defects such as shrinkage cavities, thereby obtaining a target ingot with a height-to-diameter ratio of 2.6.

[0045] In step 2, the specific process of the radial-axial deformation treatment of the four fires is as follows:

[0046] Specifically, the first fire: the target ingot is heated to 1050° C., and the holding time is 0.6D (D is the diameter of the target ingot) to ensure that the target ingot is heated through, and then deformed by upsetting first and then stretching, and the deformation reduction rate during the deformation process is 60 mm / s to obtain an intermediate billet a;

[0047] In the process of upsetting, the axial deformation is controlled to be 20%, and in the process of drawing, the radial deformation is controlled to be 23%;

[0048] Second fire: the intermediate blank a is heated to 1055°C, the holding time is 0.6D (D is the diameter of the intermediate blank a), and then deformed by upsetting first and then stretching, and the deformation reduction rate during the deformation process is 60mm / s to obtain the intermediate blank b;

[0049] In the process of upsetting, the axial deformation is controlled to be 20%, and in the process of drawing, the radial deformation is controlled to be 23%;

[0050] The third fire: the intermediate blank b is heated to 1060° C., the holding time is 0.7D (D is the diameter of the intermediate blank b), and then deformed by upsetting first and then drawing. During the deformation process, the deformation reduction rate is 55 mm / s to obtain the intermediate blank c;

[0051] In the process of upsetting, the axial deformation is controlled to 19%, and in the process of stretching, the radial deformation is controlled to 22%;

[0052] The fourth fire: the intermediate billet c is heated to 1060°C, the holding time is 0.7D (D is the diameter of the intermediate billet c), and then deformed by upsetting first and then drawing. During the deformation process, the deformation reduction rate is 55mm / s to obtain an octagonal bar billet;

[0053] In the process of upsetting, the axial deformation is controlled to be 19%, and in the process of drawing, the radial deformation is controlled to be 22%.

[0054] In step 3, the specific process of the radial deformation treatment of the three fires is as follows:

[0055] Specifically, the first fire: the bar blank is heated to 1020° C., the holding time is 0.4D (D is the diameter of the bar blank), and then stretched, and the deformation reduction rate during the stretching process is 60 mm / s to obtain an intermediate bar a;

[0056] Among them, during the stretching process, the radial deformation is controlled to be 42%;

[0057] Second fire: the intermediate bar a is heated to 1020° C., and the holding time is 0.45D (D is the diameter of the intermediate bar a), and then stretched. During the stretching process, the deformation reduction rate is equal to 60 mm / s, and the intermediate bar b is obtained;

[0058] Among them, during the stretching process, the radial deformation is controlled to be 38%;

[0059] The third fire: the intermediate bar b is heated to 1025°C, the holding time is equal to 0.45D (D is the diameter of the intermediate bar b), and then stretched. The deformation reduction rate during the stretching process is equal to 55mm / s, and a GH4169G alloy bar with a specification of Φ250 with uniform structure and excellent performance is obtained. The overall structure of the bar is shown in Figures 2 to 4 ;

[0060] During the stretching process, the radial deformation is controlled to be 28%.

[0061] On the other hand, the present embodiment provides a high-performance GH4169G high-temperature alloy round rod, which is prepared by the preparation method of the present embodiment and can remain without cracking or breaking for at least 35 hours in an environment of 680°C and loaded with a stress of 690 MPa.

[0062] On the other hand, the present embodiment provides a high-performance GH4169G high-temperature alloy round rod as described above, and its use in the preparation of aviation parts.

[0063] Example 2

[0064] On the one hand, this embodiment provides a method for preparing a high-performance GH4169G high-temperature alloy bar, comprising the following steps:

[0065] Step 1, preparing a target ingot: selecting a GH4169G alloy ingot prepared by a VIM+ESR+VAR triple smelting process, and performing homogenization treatment and machining treatment on it in sequence to obtain a target ingot with a height-to-diameter ratio of 2.0;

[0066] Step 2, blank forging: subjecting the target ingot to 5 rounds of radial and axial deformation treatment to obtain a blank;

[0067] Step 3, finished product forging: the bar blank is subjected to radial deformation treatment for 4 times to obtain a finished round bar with uniform structure and excellent performance.

[0068] Wherein, in step 1, the process of homogenizing the GH4169G alloy ingot in a high-temperature furnace is as follows: the cold material is charged into the furnace and heated to 1115°C at a heating rate of 90°C / h, kept warm for 50 hours, then heated to 1175°C at a heating rate of 2.5°C / h, kept warm for 90 hours, and finally cooled to 700°C and then taken out of the furnace and air-cooled to room temperature;

[0069] Furthermore, the cooled ingot is machined to remove surface defects such as shrinkage cavities, thereby obtaining a target ingot with a height-to-diameter ratio of 2.0.

[0070] In step 2, the specific process of the 5-fire radial-axial deformation treatment is as follows:

[0071] Specifically, the first fire: the target ingot is heated to 1020° C., and the holding time is 0.6D (D is the diameter of the target ingot) to ensure that the target ingot is heated through, and then deformed by upsetting first and then stretching, and the deformation reduction rate during the deformation process is 30 mm / s to obtain an intermediate billet a;

[0072] In the process of upsetting, the axial deformation is controlled to be 15%, and in the process of stretching, the radial deformation is controlled to be 20%;

[0073] Second fire: the intermediate blank a is heated to 1030° C., and the holding time is 0.6D (D is the diameter of the intermediate blank a), and then deformed by upsetting first and then drawing, and the deformation reduction rate during the deformation process is 30 mm / s to obtain the intermediate blank b;

[0074] In the process of upsetting, the axial deformation is controlled to be 15%, and in the process of stretching, the radial deformation is controlled to be 20%;

[0075] The third fire: the intermediate blank b is heated to 1030° C., the holding time is 0.7D (D is the diameter of the intermediate blank b), and then deformed by upsetting first and then drawing. During the deformation process, the deformation reduction rate is 35 mm / s to obtain the intermediate blank c;

[0076] In the process of upsetting, the axial deformation is controlled to be 18%, and in the process of stretching, the radial deformation is controlled to be 22%;

[0077] The fourth fire: the intermediate blank c is heated to 1060° C., the holding time is 0.6D (D is the diameter of the intermediate blank c), and then deformed by upsetting first and then drawing. During the deformation process, the deformation reduction rate is 55 mm / s to obtain the intermediate blank d.

[0078] In the process of upsetting, the axial deformation is controlled to 19%, and in the process of stretching, the radial deformation is controlled to 22%;

[0079] The fifth fire: the intermediate billet d is heated to 1070°C, and the holding time is 0.6D (D is the diameter of the intermediate billet d), and then deformed by upsetting first and then drawing. During the deformation process, the deformation reduction rate is 50mm / s to obtain an octagonal bar billet;

[0080] In the process of upsetting, the axial deformation is controlled to be 20%, and in the process of drawing, the radial deformation is controlled to be 20%.

[0081] In step 3, the specific process of the radial deformation treatment of the four fires is as follows:

[0082] Specifically, the first fire: the bar blank is heated to 1020° C., the holding time is 0.4D (D is the diameter of the bar blank), and then stretched, and the deformation reduction rate during the stretching process is 60 mm / s to obtain an intermediate bar a;

[0083] Among them, during the stretching process, the radial deformation is controlled to be 45%;

[0084] Second fire: the intermediate bar a is heated to 1020° C., and the holding time is 0.45D (D is the diameter of the intermediate bar a), and then stretched. During the stretching process, the deformation reduction rate is equal to 55 mm / s, and the intermediate bar b is obtained;

[0085] Among them, during the stretching process, the radial deformation is controlled to be 40%;

[0086] The third fire: the intermediate bar b is heated to 1025° C., the holding time is equal to 0.45D (D is the diameter of the intermediate bar b), and then stretched. The deformation reduction rate during the stretching process is equal to 50 mm / s, to obtain the intermediate bar c;

[0087] Among them, during the stretching process, the radial deformation is controlled to be 30%;

[0088] The fourth fire: the intermediate rod c is heated to 1005°C, the holding time is equal to 0.5D (D is the diameter of the intermediate rod c), and then stretched. The deformation reduction rate during the stretching process is equal to 52mm / s, and a finished round rod with uniform structure and excellent performance is obtained;

[0089] During the stretching process, the radial deformation is controlled to be 25%.

[0090] On the other hand, the present embodiment provides a high-performance GH4169G high-temperature alloy round rod, which is prepared by the preparation method of the present embodiment and can remain without cracking or breaking for at least 35 hours in an environment of 680°C and loaded with a stress of 690 MPa.

[0091] On the other hand, the present embodiment provides a high-performance GH4169G high-temperature alloy round rod as described above, and its use in the preparation of aviation parts.

[0092] Example 3

[0093] On the one hand, this embodiment provides a method for preparing a high-performance GH4169G high-temperature alloy bar, comprising the following steps:

[0094] Step 1, preparing a target ingot: selecting a GH4169G alloy ingot prepared by a VIM+ESR+VAR triple smelting process, and performing homogenization treatment and machining treatment on it in sequence to obtain a target ingot with a height-to-diameter ratio of 3.0;

[0095] Step 2, blank forging: subjecting the target ingot to 6 rounds of radial and axial deformation treatment to obtain a blank;

[0096] Step 3, finished product forging: the bar blank is subjected to radial deformation treatment for 5 times to obtain a finished round bar with uniform structure and excellent performance.

[0097] Wherein, in step 1, the process of homogenizing the GH4169G alloy ingot in a high-temperature furnace is as follows: the cold material is charged into the furnace and heated to 1130°C at a heating rate of 100°C / h, kept warm for 40 hours, then heated to 1190°C at a heating rate of 2°C / h, kept warm for 80 hours, and finally cooled to 850°C and then taken out of the furnace and air-cooled to room temperature;

[0098] Furthermore, the cooled ingot is machined to remove surface defects such as shrinkage cavities, thereby obtaining a target ingot with a height-to-diameter ratio of 3.0.

[0099] In step 2, the specific process of the 6-fire radial-axial deformation treatment is as follows:

[0100] Specifically, the first fire: the target ingot is heated to 1020° C., and the holding time is 0.6D (D is the diameter of the target ingot) to ensure that the target ingot is heated through, and then deformed by upsetting first and then stretching, and the deformation reduction rate during the deformation process is 50 mm / s to obtain an intermediate billet a;

[0101] In the process of upsetting, the axial deformation is controlled to be 25%, and in the process of stretching, the radial deformation is controlled to be 25%;

[0102] Second fire: the intermediate blank a is heated to 1030° C., and the holding time is 0.7D (D is the diameter of the intermediate blank a), and then deformed by upsetting first and then drawing, and the deformation reduction rate during the deformation process is 80 mm / s to obtain the intermediate blank b;

[0103] In the process of upsetting, the axial deformation is controlled to be 23%, and in the process of drawing, the radial deformation is controlled to be 21%;

[0104] The third fire: the intermediate blank b is heated to 1050° C., the holding time is 0.65D (D is the diameter of the intermediate blank b), and then deformed by upsetting first and then drawing. During the deformation process, the deformation reduction rate is 40 mm / s to obtain the intermediate blank c;

[0105] In the process of upsetting, the axial deformation is controlled to be 19%, and in the process of stretching, the radial deformation is controlled to be 21%;

[0106] The fourth fire: the intermediate blank c is heated to 1080° C., and the holding time is 0.6D (D is the diameter of the intermediate blank c), and then deformed by upsetting first and then drawing. During the deformation process, the deformation reduction rate is 45 mm / s to obtain the intermediate blank d;

[0107] Among them, during the upsetting process, the axial deformation is controlled to 24%, and during the stretching process, the radial deformation is controlled to 23%;

[0108] The fifth fire: the intermediate blank d is heated to 1070°C, and the holding time is 0.6D (D is the diameter of the intermediate blank d), and then deformed by upsetting first and then drawing, and the deformation reduction rate during the deformation process is 65mm / s to obtain the intermediate blank e;

[0109] In the process of upsetting, the axial deformation is controlled to be 20%, and in the process of stretching, the radial deformation is controlled to be 20%;

[0110] The sixth fire: the intermediate billet e is heated to 1070°C, the holding time is 0.65D (D is the diameter of the intermediate billet e), and then deformed by upsetting first and then drawing. During the deformation process, the deformation reduction rate is 65mm / s to obtain an octagonal bar billet;

[0111] In the process of upsetting, the axial deformation is controlled to be 16%, and in the process of drawing, the radial deformation is controlled to be 21%.

[0112] In step 3, the specific process of the radial deformation treatment of the four fires is as follows:

[0113] Specifically, the first fire: the bar blank is heated to 1005°C, the holding time is 0.6D (D is the diameter of the bar blank), and then stretched, and the deformation reduction rate during the stretching process is 50mm / s to obtain an intermediate bar a;

[0114] Among them, during the stretching process, the radial deformation is controlled to be 30%;

[0115] Second fire: the intermediate bar a is heated to 1040° C., and the holding time is 0.5D (D is the diameter of the intermediate bar a), and then stretched. During the stretching process, the deformation reduction rate is equal to 45 mm / s, and the intermediate bar b is obtained;

[0116] Among them, during the stretching process, the radial deformation is controlled to be 28%;

[0117] The third fire: the intermediate bar b is heated to 1010° C., the holding time is equal to 0.45D (D is the diameter of the intermediate bar b), and then stretched. The deformation reduction rate during the stretching process is equal to 55 mm / s, to obtain the intermediate bar c;

[0118] Among them, during the stretching process, the radial deformation is controlled to be 42%;

[0119] The fourth fire: the intermediate bar c is heated to 1025° C., the holding time is equal to 0.55D (D is the diameter of the intermediate bar c), and then stretched. The deformation reduction rate during the stretching process is equal to 40 mm / s, to obtain the intermediate bar d;

[0120] Among them, during the stretching process, the radial deformation is controlled to be 40%;

[0121] The fifth fire: the intermediate rod d is heated to 1035°C, the holding time is equal to 0.5D (D is the diameter of the intermediate rod d), and then stretched. The deformation reduction rate during the stretching process is equal to 43mm / s, and a finished round rod with uniform structure and excellent performance is obtained;

[0122] In the process of drawing, the radial deformation is controlled to be 37%.

[0123] On the other hand, the present embodiment provides a high-performance GH4169G high-temperature alloy round rod, which is prepared by the preparation method of the present embodiment and can remain without cracking or breaking for at least 35 hours in an environment of 680°C and loaded with a stress of 690 MPa.

[0124] On the other hand, the present embodiment provides a high-performance GH4169G high-temperature alloy round rod as described above, and its use in the preparation of aviation parts.

[0125] The above description is only a specific embodiment of the present invention, so that those skilled in the art can understand or implement the present invention. Various modifications to these embodiments will be apparent to those skilled in the art, and the general principles defined herein can be implemented in other embodiments without departing from the spirit or scope of the present invention.

[0126] It should be understood that the present invention is not limited to what has been described above and that various modifications and changes may be made without departing from its scope. The scope of the present invention is limited only by the appended claims.

Claims

1. A method for preparing high-performance GH4169G high-temperature alloy rods, characterized in that: The following steps are involved: Step 1, preparing a target ingot: selecting a GH4169G alloy ingot prepared by a set process, and sequentially performing homogenization treatment and machining treatment on the ingot to obtain a target ingot with a height-to-diameter ratio of 2.0 to 3.0; Step 2, blank forging: subjecting the target ingot to 4 to 6 rounds of radial and axial deformation treatment to obtain a blank; Step 3, finished product forging: subjecting the bar blank to 3 to 5 rounds of radial deformation treatment to obtain a target bar.

2. The method for preparing the high-performance GH4169G high-temperature alloy bar according to claim 1, characterized in that: In step 1, the GH4169G alloy ingot is produced by a VIM+ESR+VAR triple smelting process.

3. The method for preparing the high-performance GH4169G high-temperature alloy bar according to claim 1, characterized in that: In step 1, the process of homogenization treatment of the GH4169G alloy ingot is as follows: the cold material is charged into the furnace and heated to 1100°C-1130°C at a heating rate of 80°C / h-100°C / h, kept warm for 40h-50h, then heated to 1160°C-1190°C at a heating rate of 2°C / h-5°C / h, kept warm for 80h-100h, and finally cooled to 500°C-850°C in the furnace and air-cooled to room temperature.

4. The method for preparing the high-performance GH4169G high-temperature alloy bar according to claim 1, characterized in that: In step 2, in the radial-axial deformation treatment of 4 to 6 times, the treatment method and parameter value range of each time are the same; The radial-axial deformation process of the first fire is as follows: heating the target ingot to 1020°C to 1080°C, holding the ingot for a time greater than or equal to 0.6D, and then deforming the ingot by upsetting first and then drawing. During the deformation process, the deformation reduction rate is 30mm / s to 80mm / s to obtain an intermediate billet, and finally the intermediate billet is subjected to the radial-axial deformation process of the next fire; The D is the diameter of the bar before the current fire forging. In the first fire of the open forging, the diameter of the bar is the diameter of the target ingot.

5. The method for preparing the high-performance GH4169G high-temperature alloy bar according to claim 4, characterized in that: During the upsetting process, the axial deformation is 15% to 25%; during the drawing process, the radial deformation is 20% to 25%.

6. The method for preparing the high-performance GH4169G high-temperature alloy bar according to claim 1, characterized in that: In step 3, in the radial deformation process of 3 to 5 times, the processing method and parameter range of each time are the same; The radial deformation process of the first fire is as follows: heating the bar blank to 1005°C to 1040°C, holding the bar blank for a time greater than or equal to 0.4D, and then drawing the bar blank. During the drawing process, the deformation reduction rate is 40mm / s to 60mm / s to obtain an intermediate bar. Finally, the intermediate bar blank is subjected to the radial deformation process of the next fire. Among them, D is the diameter of the rod blank in the first fire of the finished product forging.

7. The method for preparing the high-performance GH4169G high-temperature alloy bar according to claim 6, characterized in that: During the stretching process, the radial deformation is 25% to 45%.

8. A high-performance GH4169G high-temperature alloy bar, characterized in that: The composite material is prepared by the preparation method according to any one of claims 1 to 7, and can remain without cracking or breaking for at least 35 hours in an environment of 680°C and loaded with a stress of 690MPa.

9. Use of the high-performance GH4169G high-temperature alloy bar as claimed in claim 8 in the preparation of aviation parts.

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