A high impact performance bar of gh4169 superalloy and a method of making the same

Abstract

The application belongs to the technical field of non-ferrous metal processing, and discloses a GH4169 high-temperature alloy high-impact performance bar blank and a preparation method thereof. In the forging process, the method adopts a continuous remelting mode, reduces the exposure time of the blank outside the furnace, and reduces the precipitation of grain boundary precipitates. Low-temperature insulation is adopted in the last heat, and then round dropping treatment is carried out to improve the surface quality and edge structure of the bar blank. A heat treatment process combining high-temperature solid solution heat treatment and aging treatment is adopted. After the solid solution treatment, a cooling mode with a very fast cooling speed such as water cooling (faster than air cooling) is adopted to reduce the residence time at the δ phase precipitation temperature, so as to reduce the content of the grain boundary δ phase and improve the impact performance.

Description

Technical Field

[0001] This invention belongs to the field of non-ferrous metal processing technology, specifically relating to a high-impact performance GH4169 high-temperature alloy billet and its preparation method. Background Technology

[0002] GH4169 alloy, due to its excellent strength at high temperatures, good fatigue properties, and relatively good impact toughness, has wide applications in extreme environments with high temperature, high speed, high stress, and dynamic or impact loads. These applications include components such as turbine disks and blades in aero-engines, turbopumps, connectors, and fasteners in aerospace liquid engines, as well as hot-end components in gas turbines and some components in nuclear reactors. Furthermore, GH4169 alloy maintains relatively good impact properties within a certain low-temperature range (e.g., -196℃ to room temperature), making it a key material in aerospace cryogenic propellant environments.

[0003] For components designed for service in extreme environments with high stress and dynamic or impact loads, the impact performance of GH4169 alloy needs to reach 50 J. However, the existing GH4169 alloy has relatively low impact performance, and when the deformation method and heat treatment regime are changed, the impact performance is easily improved but the strength is reduced. There is also a risk of mixed grain structure.

[0004] Therefore, there is an urgent need for a process that can improve the impact performance of GH4169 high-temperature alloy while ensuring its original strength, plasticity, and microstructure uniformity. Summary of the Invention

[0005] The purpose of this invention is to overcome the shortcomings of the prior art and to propose a high-impact performance billet of GH4169 high-temperature alloy and its preparation method.

[0006] To achieve the above objectives, the present invention adopts the following technical solution: On the one hand, see Figure 1 This invention provides a method for preparing a high-impact performance billet of GH4169 high-temperature alloy, comprising the following steps: Step 1: Ingot preparation: Prepare raw materials according to specific chemical composition percentages, and prepare ingots using a dual smelting process of vacuum induction melting + protective atmosphere electroslag remelting. Step 2, Heat treatment: The ingot is subjected to high-temperature homogenization heat treatment; Step 3, billet forging: The ingot after high-temperature homogenization heat treatment is continuously forged in 2-3 furnaces to obtain intermediate billet A. Step 4, intermediate billet forging: Intermediate billet A is subjected to multiple heats of continuous reflow and medium-temperature upsetting forging to obtain intermediate billet B; Step 5, Finished product forging: The intermediate billet B is subjected to three consecutive low-temperature large deformation upsetting and drawing forgings; after the hot billet is returned to the furnace, the last heat is held at 980~1000℃ for 0.5~1.5h, and after being taken out of the furnace, it is slammed and rounded, and the slamming deformation is controlled at 2%~6%; after forming, it is air-cooled to obtain the target billet C. Step 6, Heat treatment: The target billet C is subjected to "high temperature solution treatment + aging treatment" and then cooled to obtain a target high temperature alloy billet with high impact performance.

[0007] Furthermore, in step 1, the chemical composition and weight percentage of the ingot are as follows: C: 0.015%~0.05%, Cr: 17.00%~21.00%, Ni: 50.00%~55.00%, Ti: 0.85%~1.15%, Nb: 5.00%~5.30%, Mo: 2.80%~3.30%, Al: 0.30%~0.70%, Mn: ≤0.35%, with the balance being Fe and other trace elements.

[0008] Furthermore, in step 3, the heating temperature of the high-temperature forging is 1080~1160℃, the holding time is 2~10h, the deformation amount per upsetting is 15%~30%, and the deformation amount per drawing is 10%~30%.

[0009] Furthermore, in step 4, the heating temperature of the medium-temperature upsetting and drawing forging is 990~1060℃, the holding time is 1~2h, the deformation per upsetting is 20%~30%, and the deformation per drawing is 15%~45%.

[0010] Furthermore, in step 5, the process parameters for the low-temperature large deformation upsetting and drawing forging are as follows: the heating temperature for each heat is 990~1010℃, the holding time for the first two heats is 0.5~2h, and the deformation amount for each heat is 25%~40%.

[0011] Furthermore, in step 6, the temperature of the solution heat treatment is 960~1000℃, and the holding time is 1~1.5h.

[0012] Specifically, in step 6, the timeliness processing is divided into two stages: The temperature of the first stage is 718~730℃, and the holding time is 8~9 hours; the temperature of the second stage is 621~630℃, and the holding time is 8~9 hours.

[0013] Furthermore, in step 6, the cooling method after high-temperature solution heat treatment is water cooling or other fast-cooling methods, while the cooling method after aging treatment is air cooling. Here, the fast-cooling method after solution heat treatment results in a shorter residence time and fewer δ-phases at the precipitation temperature, which is beneficial for improving impact resistance.

[0014] It should be noted that in step 5, the holding temperature and time for the impact firing need to be selected reasonably: if the temperature is too high or the holding time is too long, it will lead to excessive re-dissolution of the precipitated phase (δ phase), resulting in grain growth and a decline in other properties; if the temperature is too low or the holding time is insufficient, it will lead to less re-dissolution of the δ phase, and the impact performance will not be significantly improved.

[0015] On the other hand, the present invention provides a GH4169 high-temperature alloy high-impact performance billet, which is prepared by some or all of the above-described high-temperature alloy high-impact performance billet preparation methods, wherein the grain size at the head and tail R / 2 of the GH4169 high-temperature alloy high-impact performance billet is ≥ grade 5.

[0016] The relevant performance parameters of the GH4169 high-temperature alloy high-impact performance billet are as follows: Impact absorption energy at room temperature KU2 ≥ 50 J, tensile strength at room temperature ≥ 1300 MPa, yield strength at room temperature ≥ 1100 MPa, elongation at room temperature ≥ 15%, reduction of area at room temperature ≥ 15%; Tensile strength at 650℃ ≥1050MPa, yield strength at 650℃ ≥900MPa, elongation at 650℃ ≥15%, reduction of area at 650℃ ≥15%.

[0017] Compared with the prior art, the present invention has the following beneficial effects: (1) The present invention uses a dual smelting process of vacuum induction melting + protective atmosphere electroslag remelting to prepare ingots, and controls the content of core chemical components to C: 0.015%~0.05%, Ti: 0.85%~1.15%, Nb: 5.00%~5.30%, which can reduce harmful low melting point inclusions in the ingot and reduce the content of sensitive gas elements such as oxygen and nitrogen, thereby achieving a high purity, dense ingot structure and uniform composition. (2) In the forging process, the present invention adopts a continuous reflow method to reduce the exposure time of the billet outside the furnace and reduce the precipitation of grain boundary precipitates; the last heat is held at a low temperature and then rounded to improve the surface quality and edge structure of the billet. The longer holding time and lower temperature in this process can ensure that the δ phase is fully dissolved and the impact performance is improved, while avoiding abnormal grain growth, which would lead to a decrease in material strength and plasticity; (3) The present invention adopts a heat treatment process that combines high-temperature solution heat treatment and aging treatment. After solution treatment, a cooling method with a fast cooling rate, such as water cooling (which is faster than air cooling), is used to reduce the residence time at the δ phase precipitation temperature, thereby reducing the content of δ phase at the grain boundary and improving the impact performance. Attached Figure Description

[0018] The accompanying drawings are incorporated in and form part of this specification, and together with the description serve to explain the principles of the invention.

[0019] To more clearly illustrate the technical solutions in the embodiments of the present invention or the prior art, the drawings used in the description of the embodiments or the prior art will be briefly introduced below. Obviously, for those skilled in the art, other drawings can be obtained based on these drawings without creative effort.

[0020] Figure 1 A flowchart illustrating a method for preparing a high-impact performance bar billet of GH4169 high-temperature alloy provided by this invention; Figure 2 The image shows the microstructure of the GH4169 high-temperature alloy billet obtained in Example 1 of this invention at a magnification of 100× at the R / 2 position, with the head end (left) and tail end (right) at the R / 2 position. Figure 3 This is a 100x high-magnification microstructure image of the head end (left) and tail end (right) of the GH4169 high-temperature alloy billet obtained in Example 2 of the present invention at position R / 2; Figure 4 This is a 100× magnified microstructure image of the head end (left) and tail end (right) of the GH4169 high-temperature alloy billet obtained in Example 3 of the present invention at position R / 2. Detailed Implementation

[0021] Exemplary embodiments will now be described in detail. The embodiments described in the following exemplary embodiments do not represent all embodiments consistent with the present invention. Rather, they are merely examples consistent with some aspects of the invention as detailed in the appended claims.

[0022] Example 1 This embodiment provides a method for preparing a high-impact performance billet of GH4169 high-temperature alloy, including the following steps: Step 1: Ingot Preparation: The ingot is prepared using a dual smelting process of vacuum induction melting + protective atmosphere electroslag remelting. The chemical composition percentage of the ingot is as follows: C: 0.015%~0.05%, Cr: 17.00%~21.00%, Ni: 50.00%~55.00%, Ti: 0.85%~1.15%, Nb: 5.00%~5.30%, Mo: 2.80%~3.30%, Al: 0.30%~0.70%, Mn: ≤0.35%, with the balance being Fe and other trace elements. Step 2: The ingots prepared by the duplex smelting process are subjected to multi-stage, multi-time high-temperature homogenization treatment; Step 3, forging: The ingot is forged in two consecutive hot forgings using a 45MN high-speed forging machine to obtain intermediate billet A1. The forging method for each hot forging is upsetting and drawing in an octagonal shape. The heating temperature is 1080℃. The first hot forging is held for 10 hours and the second hot for 2 hours. The upsetting deformation is 15% and the drawing deformation is 19%. The material is directly returned to the furnace after forging. Step 4, Intermediate Billet Forging: The intermediate billet A1 after the initial forging is returned to the furnace for three consecutive hot forgings at medium temperature to obtain intermediate billet B1. A 45MN high-speed forging machine is used. Each forging process is upsetting and drawing in an octagonal shape. The heating temperature for the third forging is 1030℃, and the heating temperature for the fourth and fifth forgings is 990℃, with a holding time of 2 hours. The material is directly returned to the furnace after each forging. The upsetting deformation is 20%, and the drawing deformation is 45%. Step 5, Finished product forging: The hot intermediate billet B1 after forging is returned to the furnace for three low-temperature large deformation upsetting forging. The sixth and seventh heating temperatures are 990℃ and held for 2 hours, with a drawing deformation of 25%. The final heating temperature is 1000℃ and held for 1.5 hours. After being taken out of the furnace, it is rounded, and the rounding deformation is controlled within 6%. After forming, it is air-cooled to obtain the target billet C1. Step 6, Heat treatment regime: The target billet C1 is subjected to "high temperature solution treatment + aging treatment" to obtain a target high temperature alloy billet (I) with high impact performance; wherein: the solution temperature is 1000℃, the holding time is 1h, and the cooling method is water cooling; aging treatment: the first stage temperature is 730℃, the holding time is 8h; the second stage is furnace cooling to 621℃, the holding time is 8h, and the cooling method is air cooling.

[0023] The final high-temperature alloy billet has a grain size of 5.5 at both the head and tail R / 2 positions, and a uniform microstructure (see...). Figure 2 The relevant performance parameters are as follows: The impact absorption energy (KU2) at room temperature is 73 J, the tensile strength at room temperature is 1375 MPa, the yield strength at room temperature is 1188 MPa, the elongation after fracture at room temperature is 19%, and the reduction of area at room temperature is 39%. The tensile strength at 650℃ is 1114MPa, the yield strength at 650℃ is 975MPa, the elongation after fracture at 650℃ is 31%, and the reduction of area at 650℃ is 56%.

[0024] Example 2 This embodiment provides a method for preparing a high-impact performance billet of GH4169 high-temperature alloy, including the following steps: Step 1: Ingot Preparation: The ingot is prepared using a dual smelting process of vacuum induction melting + protective atmosphere electroslag remelting. The chemical composition percentage of the ingot is as follows: C: 0.015%~0.05%, Cr: 17.00%~21.00%, Ni: 50.00%~55.00%, Ti: 0.85%~1.15%, Nb: 5.00%~5.30%, Mo: 2.80%~3.30%, Al: 0.30%~0.70%, Mn: ≤0.35%, with the balance being Fe and other trace elements. Step 2: The ingots prepared by the duplex smelting process are subjected to multi-stage, multi-time high-temperature homogenization treatment; Step 3, forging: The ingot is forged in two consecutive hot forgings using a 45MN high-speed forging machine to obtain intermediate billet A2. The forging method for each hot forging is upsetting and drawing in an octagonal shape. The heating temperature is 1100℃. The first hot forging is held for 8 hours and the second hot for 3 hours. The upsetting deformation is 30% and the drawing deformation is 10%. The material is directly returned to the furnace after forging. Step 4, Intermediate Billet Forging: The intermediate billet A2 after the initial forging is returned to the furnace for three consecutive hot forgings at medium temperature to obtain intermediate billet B2. A 45MN high-speed forging machine is used. Each forging process is upsetting and drawing in an octagonal shape. The heating temperature for the third forging is 1050℃, and the heating temperature for the fourth and fifth forgings is 1000℃, with a holding time of 1.5 hours. The material is directly returned to the furnace after each forging. The upsetting deformation is 30%, and the drawing deformation is 15%. Step 5, Finished product forging: The hot intermediate billet B2 after forging is returned to the furnace for three-stage low-temperature large deformation upsetting and drawing forging. The sixth and seventh heating temperatures are 1000℃ and held for 1.5 hours, with a drawing deformation of 35%. The final heating temperature is 1000℃ and held for 0.5 hours. After being taken out of the furnace, it is rounded, and the rounding deformation is controlled within 4%. After forming, it is air-cooled to obtain the target billet C2. Step 6, Heat treatment regime: The target billet C2 is subjected to "high temperature solution treatment + aging treatment" to obtain a target high temperature alloy billet (II) with high impact performance; wherein, the solution temperature is 980℃, the holding time is 1h, and the cooling method is water cooling; the aging treatment: the first stage temperature is 720℃, the holding time is 9h; the second stage is furnace cooling to 625℃, the holding time is 9h, and the cooling method is air cooling.

[0025] The final high-temperature alloy billet has a grain size of 6.5 at both the head and tail R / 2 positions, and a uniform microstructure (see...). Figure 3 The relevant performance parameters are as follows: The impact absorption energy (KU2) at room temperature is 69 J, the tensile strength at room temperature is 1426 MPa, the yield strength at room temperature is 1211 MPa, the elongation after fracture at room temperature is 20%, and the reduction of area at room temperature is 41%. The tensile strength at 650℃ is 1146MPa, the yield strength at 650℃ is 1001MPa, the elongation after fracture at 650℃ is 24%, and the reduction of area at 650℃ is 59%.

[0026] Example 3 This embodiment provides a method for preparing a high-impact performance billet of GH4169 high-temperature alloy, including the following steps: Step 1: Ingot Preparation: The ingot is prepared using a dual smelting process of vacuum induction melting + protective atmosphere electroslag remelting. The chemical composition percentage of the ingot is as follows: C: 0.015%~0.05%, Cr: 17.00%~21.00%, Ni: 50.00%~55.00%, Ti: 0.85%~1.15%, Nb: 5.00%~5.30%, Mo: 2.80%~3.30%, Al: 0.30%~0.70%, Mn: ≤0.35%, with the balance being Fe and other trace elements. Step 2: The ingots prepared by the duplex smelting process are subjected to multi-stage, multi-time high-temperature homogenization treatment; Step 3, forging: The ingot is forged in two consecutive hot forgings using a 45MN high-speed forging machine to obtain intermediate billet A3. The forging method for each hot forging is upsetting and drawing in an octagonal shape. The heating temperature is 1160℃. The first hot forging is held for 5 hours, and the second hot for 5 hours. The upsetting deformation is 20%, and the drawing deformation is 30%. The material is directly returned to the furnace after forging. Step 4, Intermediate Billet Forging: The intermediate billet A3 after the initial forging is returned to the furnace for three consecutive hot forgings at medium temperature to obtain intermediate billet B3. A 45MN high-speed forging machine is used. Each forging process is upsetting and drawing in an octagonal shape. The heating temperature for the third forging is 1080℃, and the heating temperature for the fourth and fifth forgings is 1020℃, with a holding time of 1 hour. The material is directly returned to the furnace after each forging. The upsetting deformation is 27%, and the drawing deformation is 32%. Step 5, Finished product forging: The hot intermediate billet B3 after forging is returned to the furnace for three low-temperature large deformation upsetting and drawing forging. The sixth and seventh heating temperatures are 1010℃ and held for 0.5h, with a drawing deformation of 40%. The final heating temperature is 980℃ and held for 1h. After being taken out of the furnace, it is rounded, and the rounding deformation is controlled within 2%. After forming, it is air-cooled to obtain the target billet C3. Step 6, Heat treatment regime: The target billet C3 is subjected to "high temperature solution treatment + aging treatment" to obtain a target high temperature alloy billet (III) with high impact performance; wherein, the solution temperature is 960℃, the holding time is 1.5h, the cooling method is slow cooling, the aging treatment: the first stage temperature is 718℃, the holding time is 8h; furnace cooling to 630℃, the holding time is 8h, and the cooling method is air cooling.

[0027] The final high-temperature alloy billet has a grain size of grade 7 at both the head and tail R / 2 positions, and a uniform microstructure (see...). Figure 4 The relevant performance parameters are as follows: The impact absorption energy (KU2) at room temperature is 65 J, the tensile strength at room temperature is 1418 MPa, the yield strength at room temperature is 1228 MPa, the elongation after fracture at room temperature is 21%, and the reduction of area at room temperature is 43%. The tensile strength at 650℃ is 1126MPa, the yield strength at 650℃ is 1018MPa, the elongation after fracture at 650℃ is 32%, and the reduction of area at 650℃ is 63%.

[0028] Comparative Example 1 Based on Example 2, this comparative example provides a method for preparing a high-impact performance billet (IV) of GH4169 high-temperature alloy. The difference from Example 2 is that in step 6, the cooling method after solution heat treatment is air cooling.

[0029] Although the grain size at the head and tail R / 2 positions of the final high-temperature alloy billet is grade 7.5 and the microstructure is uniform, the impact absorption energy KU2 at room temperature is only 45J, which cannot meet the service requirements of extreme environments under dynamic or impact loads.

[0030] Comparative Example 2 Based on Example 2, this comparative example provides a method for preparing a high-impact performance billet (V) of GH4169 high-temperature alloy. The difference from Example 2 is that in step 6, the cooling method after solution heat treatment is slow cooling.

[0031] Although the grain size at the head and tail R / 2 positions of the final high-temperature alloy billet is grade 6.5 and the microstructure is uniform, the impact absorption energy KU2 at room temperature is only 30J, which is far from meeting the service requirements of extreme environments under dynamic or impact loads.

[0032] Comparative Example 3 Based on Example 2, this comparative example provides a method for preparing a GH4169 high-temperature alloy high-impact performance billet (six), which differs from Example 2 in that: in step 5, the final heat-striking and holding time is 0.3h.

[0033] Although the grain size at the head and tail R / 2 positions of the final high-temperature alloy billet is grade 7 and the microstructure is uniform, the impact absorption energy KU2 at room temperature is only 43J, which cannot meet the service requirements of extreme environments under dynamic or impact loads.

[0034] Comparative Example 4 Based on Example 2, this comparative example provides a method for preparing a high-impact performance GH4169 high-temperature alloy billet (VII), which differs from Example 2 in that: in step 5, the final heat-shrinking and holding time is 2 hours.

[0035] Although the impact absorption energy KU2 at room temperature is 70J, the grain size at the head and tail R / 2 positions of the final high-temperature alloy billet is only grade 4.

[0036] Comparative Example 5 Based on Example 2, this comparative example provides a method for preparing a high-impact performance billet (eight) of GH4169 high-temperature alloy. The difference from Example 2 is that in step 5, the final rounding and shaving process is not performed.

[0037] Although the grain size at the head and tail R / 2 positions of the final high-temperature alloy billet is grade 7.5, the impact absorption energy KU2 at room temperature is only 35J, which cannot meet the service requirements of extreme environments under dynamic or impact loads.

[0038] In summary, the high-impact performance billet preparation method of the present invention can obtain high-temperature alloy billets with good microstructure uniformity (grain size ≥ 5 grade) and high impact performance (impact absorption energy KU2 ≥ 50 J at room temperature). While ensuring the original strength, plasticity and microstructure uniformity, it can improve its impact performance, which has high application value in actual industrial production.

[0039] The above description is merely a specific embodiment of the present invention, enabling those skilled in the art to understand or implement the invention. Various modifications to these embodiments will be readily apparent to those skilled in the art, and the general principles defined herein may be implemented in other embodiments without departing from the spirit or scope of the invention.

[0040] It should be understood that the present invention is not limited to the content already described above, and various modifications and changes can 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 a high-impact performance billet of GH4169 high-temperature alloy, characterized in that, Includes the following steps: Step 1: Ingot preparation: Prepare raw materials according to specific chemical composition percentages, and prepare ingots using a dual smelting process of vacuum induction melting + protective atmosphere electroslag remelting. Step 2: Perform high-temperature homogenization heat treatment on the ingot; Step 3, billet forging: The ingot after high-temperature homogenization heat treatment is continuously forged in 2-3 furnaces to obtain intermediate billet A. Step 4, intermediate billet forging: Intermediate billet A is subjected to multiple heats of continuous reflow and medium-temperature upsetting forging to obtain intermediate billet B; Step 5, Finished product forging: The intermediate billet B is subjected to three consecutive low-temperature large deformation upsetting and drawing forgings; after the hot billet is returned to the furnace, the last heat is held at 980~1000℃ for 0.5~1.5h, and after being taken out of the furnace, it is slammed and rounded, and the slamming deformation is controlled at 2%~6%; after forming, it is air-cooled to obtain the target billet C. Step 6, Heat treatment: The target billet C is subjected to "high temperature solution treatment + aging treatment" and then cooled to obtain a target high temperature alloy billet with high impact performance.

2. The method for preparing the high-impact performance bar billet of GH4169 high-temperature alloy according to claim 1, characterized in that, In step 1, the chemical composition and weight percentage of the ingot are as follows: C: 0.015%~0.05%, Cr: 17.00%~21.00%, Ni: 50.00%~55.00%, Ti: 0.85%~1.15%, Nb: 5.00%~5.30%, Mo: 2.80%~3.30%, Al: 0.30%~0.70%, Mn: ≤0.35%, with the balance being Fe and other trace elements.

3. The method for preparing the high-impact performance billet of GH4169 high-temperature alloy according to claim 1, characterized in that, In step 3, the heating temperature of the high-temperature forging is 1080~1160℃, the holding time is 2~10h, the deformation amount per upsetting is 15%~30%, and the deformation amount per drawing is 10%~30%.

4. The method for preparing the high-impact performance billet of GH4169 high-temperature alloy according to claim 1, characterized in that, In step 4, the heating temperature of the medium-temperature upsetting and drawing forging is 990~1060℃, the holding time is 1~2h, the deformation per upsetting is 20%~30%, and the deformation per drawing is 15%~45%.

5. The method for preparing the GH4169 high-impact alloy high-impact performance billet according to claim 1, characterized in that, In step 5, the process parameters for the low-temperature large deformation upsetting and drawing forging are as follows: the heating temperature for each heat is 990~1010℃, the holding time for the first two heats is 0.5~2h, and the deformation amount for each heat is 25%~40%.

6. The method for preparing the high-impact performance billet of GH4169 high-temperature alloy according to claim 1, characterized in that, In step 6, the solution heat treatment temperature is 960~1000℃, and the holding time is 1~1.5h.

7. The method for preparing GH4169 high-impact alloy high-impact performance billet according to claim 1, characterized in that, In step 6, the timeliness processing is divided into two stages: The temperature of the first stage is 718~730℃, and the holding time is 8~9 hours; the temperature of the second stage is 621~630℃, and the holding time is 8~9 hours.

8. The method for preparing the high-impact performance billet of GH4169 high-temperature alloy according to claim 1, characterized in that, In step 6, water cooling is used for the cooling after high-temperature solution heat treatment, and air cooling is used for the cooling after aging treatment.

9. A high-impact performance billet of GH4169 high-temperature alloy, prepared by the method for preparing high-impact performance billets of high-temperature alloys as described in any one of claims 1 to 8, characterized in that, The grain size at half the radius of the head and tail end faces of the GH4169 high-temperature alloy high-impact performance bar billet is ≥ grade 5.

10. The GH4169 high-impact alloy billet according to claim 9, characterized in that, The relevant performance parameters of the GH4169 high-temperature alloy high-impact performance billet are as follows: Impact absorption energy at room temperature KU2 ≥ 50 J, tensile strength at room temperature ≥ 1300 MPa, yield strength at room temperature ≥ 1100 MPa, elongation at room temperature ≥ 15%, reduction of area at room temperature ≥ 15%; Tensile strength at 650℃ ≥1050MPa, yield strength at 650℃ ≥900MPa, elongation at 650℃ ≥15%, reduction of area at 650℃ ≥15%.

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