WO2005073515A1

WO2005073515A1 - Disk material

Info

Publication number: WO2005073515A1
Application number: PCT/JP2004/000887
Authority: WO
Inventors: Satoshi Takahashi; Sadao Nishikiori; Kazunori Tahara; Yusuke Ueda; Mitsuhiro Takekawa
Original assignee: Ishikawajima-Harima Heavy Industries Co., Ltd.
Priority date: 2004-01-30
Filing date: 2004-01-30
Publication date: 2005-08-11

Abstract

Disk material (20) for use in, for example, turbine disks of a jet engine and a gas turbine engine, which disk material (20) is comprised of a Ϝ’ precipitation strengthened Ni-based alloy having fine crystal regions of 20 μm or less crystal grain diameter and coarse crystal regions of 70 to 130 μm crystal grain diameter.

Description

Specification

Disc material Technical field

The present invention relates to a ring-shaped or disk-shaped disc material used for an evening bin disc or the like. Background art

The disk material used for the turbine disk of a jet engine and a gas turbine engine is mainly composed of a Ni-base superalloy precipitation-strengthened by the α, (Ni ₃ Al) phase. Among these disc materials, there is a dual property disc having different strength characteristics required for an outer peripheral portion and an inner peripheral portion. Specifically, the outer periphery of the disk that comes into contact with the high-temperature combustion gas must have high-temperature strength, and the inner periphery of the disk, which is the joint with the rotating shaft, must have fatigue strength.

Here, one means for increasing the high-temperature strength is to increase the crystal grain size of the metal crystals constituting the disk material. Further, as one means for increasing the fatigue strength, a reduction in the crystal grain size of the metal crystals constituting the disk material can be cited. As can be seen from these facts, high-temperature strength and fatigue strength are contradictory properties, and it is difficult to achieve both at a high level.

U.S. Pat. No. 5,326,409 is known as a disc material having dual properties. The invention described in this specification involves immersing the outer periphery of a disc material in a salt bath (chloride bath) at about 1200 ° C. and rotating the disc material by 60 ° over the entire circumference. is there. In the invention described in this specification, a single heat treatment in which a disk material is immersed in a salt bath is used to increase the size of metal crystal grains in the outer peripheral portion of the disk.

By the way, the heat treatment method of the invention described in U.S. Patent No. 5,326,409,

(1) Solid solution of precipitates on grain boundaries that act as pinning of grain boundaries

(2) After the precipitates are dissolved, the temperature Amplify

These two processes were performed by a single heat treatment.

For this reason, the following problems may occur.

(a) If the temperature difference between the solid solution temperature of the precipitates on the crystal grain boundaries and the melting start temperature of the alloy is small, a part of the crystal grain boundaries undergoes partial melting during heat treatment.

(b) When the heat treatment is performed for a long time, the temperature rise of the inner circumference of the disk is predicted. As a result, there is a possibility that the crystal grains of the metal crystal not only at the outer peripheral portion of the disk but also at the inner peripheral portion of the disk become coarse.

(c) Since a high-temperature (about 1200 ° C) salt bath is used for heat treatment, it is very difficult to handle the salt bath during heat treatment. Disclosure of the invention

One embodiment of the present invention is a disk material composed of a 7 ′ precipitation-strengthened Ni-based alloy, in which a fine crystal part having a crystal grain size of 20 m or less and a coarse crystal part having a crystal grain size of 70 to 130 zm are provided. And. As a result, a disc material having a fine crystal part having excellent fatigue strength and a coarse crystal part having high temperature strength is obtained.

Another aspect of the present invention is a disk material composed of an α ′ precipitation strengthened Ni-based alloy, wherein a fine crystal part having an α ′ phase precipitated at a crystal grain boundary and having a crystal grain size of 20 m or less; no precipitation of § ⁵ phase in the grain boundary, grain size is one having a large crystal of 70 to 130 m. As a result, a disc material having fine crystal parts having excellent fatigue strength and coarse crystal parts having high temperature strength is obtained.

Another embodiment of the present invention relates to a method in which a part of a disk body composed of an α ′ precipitation strengthened Ni After performing the first heat treatment of heating for a short time in the temperature range of 10 ° C higher, the entire disc body is heated 100 ° C lower than the heating temperature of the first heat treatment to the heating temperature of the first heat treatment. This is to perform a second heat treatment of heating at a temperature lower by 10 ° C. for a predetermined time. As a result, a part of the disk body is formed in a coarse crystal part having a crystal grain size of 70 to: and the remaining part of the disk body is formed in a fine crystal part having a crystal grain size of the following. Characteristics can be achieved at a high level.

Further, another embodiment of the present invention relates to a fine crystal part having a crystal grain size of 20 m or less and a coarse crystal part having a crystal grain size of 70 to 130 μm, which is formed of an α 'precipitation strengthened Ni-based alloy. It is an evening bin disc manufactured using a disc material having the following. As a result, a turbine disk having a high level of high-temperature strength and fatigue strength can be obtained.

Still another embodiment of the present invention is a turbine engine manufactured using the above-described turbine disk. As a result, a highly reliable evening bin engine can be obtained. Brief Description of Drawings

FIG. 1 is a view for explaining a method of manufacturing a disk material according to a preferred embodiment of the present invention.

FIG. 2 is a perspective view of a disk material according to a preferred embodiment of the present invention. FIG. 3 is a diagram showing a thermal analysis result of an as-forged material composed of N18. 4 (a) to 4 (d) show the relationship between the heat treatment temperature, the grain growth behavior, and the solid solution behavior of the as-forged material composed of N18. Fig. 4 (a) shows the as-forged material, Fig. 4 (b) shows the heat-treated material at 1160 ° C x 4h, Fig. 4 (c) shows the heat-treated material at 1180 ° C x 4h, and Fig. 4 (d) shows the temperature at 1200 ° C x 4h. It is a structure observation figure of a heat-treated material. '

Fig. 5 is a diagram showing the relationship between the heat treatment time and the crystal grain size when the as-forged material shown in Fig. 4 (a) was heat-treated at 1160 ° C, 1180 ° C, and 1200 ° C, respectively. .

Figs. 6 (a) to 6 (c) are microstructure observations of the as-forged material shown in Fig. 4 (a) when heat-treated at 1220 ° C. Fig. 6 (a) shows the structure of the heat-treated material at 1220 ° C x 0.5h, Fig. 6 (b) shows the structure of the heat-treated material at 1220 ° C x 1.0h, and Fig. 6 (c) shows the structure of the heat-treated material at 1220 ° C x 2.0h. is there.

FIGS. 7 (a), 7 (b), and 7 (c) are enlarged views of FIGS. 6 (a), 6 (b), and 6 (c), respectively.

FIG. 8 is a diagram for explaining a method of manufacturing a disk material according to a preferred embodiment of the present invention. The as-forged material shown in FIG. 4 (a) is subjected to first heating at 1200 ° C. for 0.5 h. place FIG. 9 is a view showing the relationship between the heat treatment time of the second heat treatment and the crystal grain size of the outer peripheral portion of the disk when performing the second heat treatment at 1180 ° C. after the heat treatment.

Fig. 9 (a) to Fig. 9 (c) show that the as-forged material shown in Fig. 4 (a) was subjected to the first heat treatment at 1200 ° C x 0.5h, and then to the second heat treatment at 1180 ° C. FIG. 8 is a view showing a relationship between a heat treatment time of a second heat treatment and a crystal grain size of a disk outer peripheral portion when performing a treatment. Fig. 9 (a) shows the second heat treatment material at 1180 ° C xlh, Fig. 9 (b) shows the second heat treatment material at 1180 ° C x 2h, and Fig. 9 (c) shows the second heat treatment at 1180 ° C x 4h. It is a processing material. BEST MODE FOR CARRYING OUT THE INVENTION

The present invention will be described in more detail with reference to the accompanying drawings. As shown in FIG. 2, the disk material 20 according to a preferred embodiment of the present invention has a ring shape and a disk shape made of an α ′ precipitation strengthened Ni-based alloy, and has a crystal grain size. It has a fine crystal part of 20 μm or less and a coarse crystal part having a crystal grain size of 70 to 130 μm, preferably 80 to 120 zm, more preferably 90 to UO m. Specifically, the fine crystal part is the inner peripheral part 21 of the disk, the coarse crystal part is the outer peripheral part 22 of the disk, and the crystal grain boundaries of the metal crystals in the inner peripheral part 21 of the disk are a, (Ni ₃ Al ) A phase has precipitated. A hole 23 is formed at the center of the disk material 20.

Here, a, as the precipitation-strengthened Ni-based alloy, all of those conventionally used in jet engines and evening bin discs of gas evening bin engines can be applied, and are not particularly limited. Absent. For example, various INC0NEL (registered trademark), various INCOLOY (registered trademark), various NIMONIC (registered trademark), various UDIMET alloy (registered trademark), Waspalloy (registered trademark), Hastelloy (registered trademark), etc. are applicable. And preferably N18 (registered trademark).

The average particle size of the ァ ′ on the crystal grain boundary (the ァ ′ on the crystal grain boundary in the disk body 10 described later) is 1 to 10 m, preferably 2 to 5 μm. The ratio of the 上の ′ on the crystal grain boundary to the metal crystal in the inner peripheral portion 21 of the disk is represented by the area ratio (the area occupied by the '′ on the crystal grain boundary / the entire metal crystal in the inner peripheral portion 21 of the disk). (Area) 0.05 to 0.25, preferably 0.10 to 0.20. Next, a method for manufacturing a disk material according to a preferred embodiment of the present invention will be described in order, showing the reasons for limiting the numerical range.

§ ³ precipitation strengthened N i based alloys, specifically raised forging Mom material gradually composed of N 18, shows the thermal analysis results of the Atsushi Nobori process in FIG. The horizontal axis in FIG. 3 indicates temperature (° C), and the vertical axis indicates temperature difference ΔΤ. The term “temperature difference ΔΤ” here means that two heat-resistant containers are prepared, the material is forged in one container, the other container is emptied, and each container is gradually heated and the temperature of each container is increased. Is measured using a temperature measuring device (for example, a thermocouple), and the temperature difference of each container is shown as "temperature difference ΔΤ".

As shown in Fig. 3, when comparing the actual temperature difference curve 30 with the mass carp 31 for the as-forged material composed of N18, the temperature difference curve 30 is higher than the master force 31. Dissolution occurs at the location where it is located. Among these portions, the shaded region 32 is a region where y in the crystal grain forms a solid solution, and its solid solution temperature is about 1030 to 1070 ° C. The hatched region 33 is a region where the solid solution on the crystal grain boundary is dissolved, and its solid solution temperature is about U70 to 1190 ° C.

Therefore, in the heat-treated material shown in Fig. 4 (b) where the as-forged N18 material shown in Fig. 4 (a) was heat-treated at 1160 ° C for 4h, the a 'that had precipitated on the grain boundaries was There was not much solid solution, and many a remained on the crystal grain boundaries. Since the crystal grain boundaries are pinned by this y, the crystal grains of the heat-treated material in Fig. 4 (b) were small, not much different from the as-forged material in Fig. 4 (a).

However, in the heat-treated material shown in Fig. 4 (c) where the as-forged material was subjected to a heat treatment at 1180 ° C x 4h, the a 'that had precipitated on the crystal grain boundaries due to the heat treatment was considerably dissolved. The amount of α 'on the grain boundaries was smaller than that of the heat-treated material of (b). As a result, the pinning effect at the grain boundaries was weakened, and the crystal grain of the heat-treated material in Fig. 4 (c) was larger than that of the heat-treated material in Fig. 4 (b).

In addition, in the heat-treated material shown in Fig. 4 (d) where the as-forged material is subjected to a heat treatment at 1200 ° C for 4h, the α 'that has precipitated on the crystal grain boundaries due to the heat treatment is completely (or almost completely) dissolved. However, no (or almost no) α ′ was precipitated on the crystal grain boundaries. As a result, the pinning effect of the grain boundaries further weakened, and the heat-treated material shown in Fig. The crystal grains became coarse. However, some of the grains were still small, and the size of the grains varied.

Next, Fig. 5 shows the relationship between the heat treatment time and the crystal grain size when the as-forged material shown in Fig. 4 (a) was heat-treated at 1160 ° C, 1180 ° C, and 1200 ° C, respectively. . The horizontal axis in Fig. 5 shows the heat treatment time (h), and the vertical axis shows the crystal grain size (〃m).

As shown by the line 51 in FIG. 5, when the heat treatment is performed at 1160 ° C., even if the heat treatment time is prolonged, the crystal grain size remains almost 10 μm and hardly changes.

On the other hand, as shown by the line 52 in FIG. 5, when the heat treatment is performed at 1180 ° C., the crystal grain size increases as the heat treatment time increases. This is because, by increasing the heat treatment time, the α ′ precipitated on the crystal grain boundaries gradually becomes solid solution, and the pinning effect gradually weakens. Further, as shown by the line 53 in FIG. 5, when the heat treatment was performed at 1200 ° C., the crystal grain size was coarse, approximately 60 μm. Was this precipitated on the grain boundaries? Is completely (or almost completely) dissolved and secondary recrystallization occurs. However, when heat treatment is performed at 1200 ° C for more than 2 hours, the crystal grain size starts to vary. The variation is due to the fact that some crystal grains are coarsened by the heat treatment, and the coarsened crystal grains prevent the adjacent crystal grains from being coarsened.

As described above, in order to coarsen the crystal grains of the as-forged material shown in FIG. 4A, it is preferable to perform the heat treatment at a temperature of 1170 ° C. or more, preferably 1180 ° C. or more. When the heat treatment is performed at 1200 ° C., the heat treatment time is set to 2.011 or less, preferably 1. Oh or less.

Next, evaluation was performed for the case where the heat treatment temperature of the as-forged material shown in Fig. 4 (a) was higher than 1200 ° C. Figures 6 (a) to 6 (c) show the microstructure observations of the as-forged material shown in Fig. 4 (a) when heat-treated at 1220 ° C.

The heat-treated material at 1220 ° C x 0.5h shown in Fig. 6 (a), the heat-treated material at 1220 ° CxlOh shown in Fig. 6 (b), and the heat-treated material shown in Fig. 6 (c); l220 ° C x 2.0h In each case, all (or almost all) of α ′ precipitated on the crystal grain boundaries was dissolved. However, as shown in Figs. 7 (a) to 7 (c), the enlarged views of Figs. 6 (a) to 6 (c) show that a part of the grain boundary part Melting was observed (Fig. 7 (a) to Fig. 7 (c), black part in the center). From this, heat treatment of the as-forged material at 1220 ° C as shown in Fig. 4 (a) requires partial melting at a part of the crystal grain boundary even for a short time heat treatment. This is not desirable.

Based on the above, the present inventors have found that a disk material 20 having a disk inner peripheral portion 21 of a fine crystal portion and a disk outer peripheral portion 22 of a coarse crystal portion can be obtained by a single heat treatment. Instead, it was found that two-stage heat treatment was required to obtain the disc material 20. Further, the present inventors have found the temperature and time of each heat treatment in the two-step heat treatment.

As shown in FIG. 1, a method of manufacturing a disk material according to a preferred embodiment of the present invention includes a disk body 10 made of an α ′ precipitation-strengthened Ni-based alloy precipitation-strengthened by an α ′ phase. After performing a first heat treatment in which the outer periphery of the disk (partially) 12 is heated for a short time in a temperature range from the solid solution temperature of the α ′ phase to 10 ° C. higher than the solid solution temperature, the disk body 1 0 is subjected to a second heat treatment for heating for a predetermined time in a range of 100 ° C. lower than the heat temperature of the first heat treatment to 10 ° C. lower than the heat temperature of the first heat treatment. .

More specifically, for example, after a rotating shaft 14 is fitted into a hole 13 of a 0400 mm disk body 10 having a hole 13 in the center, the disk body 10 becomes a high-frequency induction heating device 15 Is set to The high-frequency induction heating device 15 has a cylindrical sleeve portion 16, flange portions 17 a and 17 b projecting radially inward from both ends in the height direction of the sleeve portion 16, and a high-frequency current (not shown). And a lead member. The height of the sleeve portion 16 is formed larger than the thickness of the disk body 10. The space surrounded by the sleeve section 16 and the flange sections 17a and 17b forms a high-frequency induction heating section, and the disk outer peripheral section 12 of the disk body 10 is located in this space and set. Is made. In FIG. 1, the shape of the high-frequency induction heating device 15 is a shape obtained by bisecting a ring. However, the shape is not particularly limited as long as the shape is such that only the disk outer peripheral portion 12 can be induction-heated. The disk outer peripheral portion 12 is, for example, a portion having a width of 10 cm from the outer edge of the disk body 10.

First, as a first step, the heating temperature of the high-frequency induction heating device 15 is reduced. After adjusting the high-frequency current value so as to be 1170 to 1200 ° C., by rotating the rotating shaft 14, the disk body 10 is rotated. Thus, the outer peripheral portion 12 of the disk body 10 is subjected to high-frequency induction heating over the entire circumference, and the first heat treatment is performed. Heating time by high-frequency induction heating is 0.1 to 2.01, preferably 0.1 to: Since LO h is short, heat generated by high-frequency induction heating is applied to the inner peripheral portion 11 of the disk 10. Has little effect. In addition, by circulating a cooling medium 19 inside the rotating shaft 14 and cooling the inner peripheral portion 11 of the disk, the inner peripheral portion 1 of the disk by high-frequency induction heating is cooled.

1 can be further reduced. By this high-frequency induction heating, the precipitate (α ′ phase) that has precipitated on the crystal grain boundaries in the outer peripheral portion 12 of the disk is dissolved. Further, in the stage of the first heat treatment, the crystal grain size of the metal crystal in the outer peripheral portion 12 of the disk is not controlled.

Next, as a second step, the disk body 10 is placed in a resistance furnace and heated to perform a second heat treatment on the entire disk body 10. The heating temperature in the resistance furnace is 1070 ~; 1190 ° C, preferably 1100 ~: U90 ° C, and the heating time is 0.5 ~ 10h, preferably 0.5 ~ 4.0h. By controlling the heating temperature and the heating time of the second heat treatment, the crystal grain size in the outer peripheral portion 12 of the disk body is controlled. More specifically, the α ′ phase suppresses the coarsening of the crystal grains due to the pinning effect, but the α ′ phase on the crystal grain boundaries in the outer peripheral portion 12 of the disk is reduced by the first heat treatment. It has already dissolved. As a result, after the second heat treatment,

While the crystal grains of the metal crystal in 11 remain fine, the crystal grains of the metal crystal in the outer peripheral portion 12 of the disk are coarsened. In addition, by the second heat treatment, a solution treatment is performed on the entire disc body 10, so that the distortion of the inner peripheral portion 11 of the disc is alleviated and eliminated, and the fatigue strength is improved.

As a result, the inner peripheral part of the disk 11 is a fine crystal part with a crystal grain size of 20 zm or less.

The disk outer periphery 12 is formed on the (disk inner periphery 21) in a large crystal part (disk outer periphery 22) having a crystal grain size of 70 to 130 m, and the disk material 20 shown in FIG. Is obtained.

After subjecting the as-forged material shown in Fig. 4 (a) to the first heat treatment at 1200 ° C x 0.5 h, FIG. 8 shows the relationship between the heat treatment time of the second heat treatment and the crystal grain size of the outer peripheral portion of the disk when the second heat treatment is performed at n80 ° C.

For example, as shown by the line 81 in FIG. 8, after subjecting the as-forged material shown in FIG. 4 (a) to the first heat treatment of 120 ° TCx (). 5h, the second heat treatment at 1180 ° C. The crystal grain size of the treated heat-treated material at the outer peripheral portion 22 of the disk was slightly more than 301 11 when the second heat treatment time was 0.5 h. Thereafter, as the heat treatment time becomes longer, the crystal grain size in the outer peripheral portion 22 of the disk becomes coarse, and when the processing time of the second heat treatment is 4 h, the crystal grain size in the outer peripheral portion 22 of the disk becomes larger. It was about 85 m. As shown in Figs. 9 (a) to 9 (c), as shown in Figs. 9 (a) to 9 (c), as the processing time of the second heat treatment increases to lh, 2h, and 4h, It can be seen that the crystal grains of the metal crystals are getting coarser.

On the other hand, as shown by the line 82 in FIG. 8, the crystal grain size at the disk outer peripheral portion 22 of the heat-treated material obtained by performing a single heat treatment at 1180 ° C. on the as-forged material shown in FIG. However, even after the heat treatment for 8 hours, it was only over 20 zm. As shown by the line 83 in FIG. 8, the crystal grain size at the disk outer peripheral portion 22 of the heat-treated material obtained by performing a single heat treatment at 1160 ° C. on the as-forged material shown in FIG. Even if the heat treatment time was prolonged, there was almost no change, only 10 m or more.

As described above, the heat-treated material indicated by the line 81 using the method of manufacturing the disc material 20 according to the present embodiment is subjected to the first heat treatment at 1200 ° C. for 0.5 h, and then to the heat treatment of the first heat treatment. By performing the second heat treatment at a temperature 20 ° C. lower than the temperature, even if the processing time of the second heat treatment is as short as 4 hours, the crystal grains of the metal crystals in the outer peripheral portion 22 of the disk are reduced by about 85%. m could be coarsened.

According to the method of manufacturing the disk material 20 according to the present embodiment, the first heat treatment, which is the first step, is performed by solidifying the a ′ phase on the crystal grain boundaries in the disk outer peripheral portion 12 of the disk body 10. For the purpose of melting, the crystal grains of the metal crystal in the outer peripheral portion 12 of the disk are not made coarse. Therefore, a heat treatment temperature range that does not cause partial melting at the disk outer peripheral portion 12 can be selected and set, and as a result, partial melting does not occur at the disk outer peripheral portion 12. Further, according to the method for manufacturing the disk material 20 according to the present embodiment, the first heat treatment for partially heating the disk outer peripheral portion 12 of the disk body 10 is intended only for solid solution of the a ′ phase. There is no need to perform heat treatment for a long time. In other words, since the first heat treatment is a short-time heat treatment, there is no possibility that the temperature will rise due to the thermal effect on the inner peripheral portion 11 of the disk, and the effective thermal effect will be effective only on the outer peripheral portion 12 of the disk. Can be given.

Furthermore, according to the method of manufacturing the disc material 20 according to the present embodiment, after performing the first heat treatment for 1170 to 1200 ° C. x a short time, the heating temperature of the first heat treatment is reduced by 100 ° C. By performing the second heat treatment in a temperature range from a low temperature to a temperature lower by 10 ° C. than the heating temperature of the first heat treatment, even if the processing time of the second heat treatment is short, the outer peripheral portion 22 of the disk can be used. The crystal grains of the metal crystal can be made coarse.

Further, in the method of manufacturing the disk material 20 according to the present embodiment, it is preferable to perform the first heat treatment using the high-frequency induction heating device 15. In this case, compared with the invention described in US Pat. No. 5,326,409 using a salt bath, the heat treatment can be performed in a shorter time, and the outer peripheral portion 12 Only the effective thermal effects can be exerted. In addition, since the high-frequency induction heating device 15 is used instead of the salt bath, the operation at the time of the heat treatment becomes simpler and safer.

Further, in the method of manufacturing disk 20 according to the present embodiment, a salt bath may be used for the first heat treatment. In this case, the bath temperature of the salt bath is adjusted to a temperature 10 ° C higher than the solid solution temperature of the solid phase to the solid solution temperature, specifically 1170 to 1200 ° C, and the disk body 10 is rotated. The first heat treatment is performed by immersing the disk outer peripheral portion 12 in a salt bath for a short time.

The disk material 20 according to the present embodiment has a disk inner peripheral portion 21 of a fine crystal portion and a disk outer peripheral portion 22 of a coarse crystal portion. Therefore, the inner peripheral portion has excellent fatigue strength, and the outer peripheral portion. Is a dual property disc material with excellent high temperature strength.

Further, in the disk material 20 according to the present embodiment, the case where the inner peripheral portion 21 of the disk is a fine crystal portion and the outer peripheral portion 22 of the disk is a coarse crystal portion has been described, but the present invention is not particularly limited to this. . For example, the inner peripheral part 21 of the disk is a coarse crystal part, The disk outer peripheral portion 22 may be a fine crystal portion.

On the other hand, the turbine disk according to the present embodiment is manufactured using the disk material 20. As a result, it is possible to obtain an evening bin disc in which the outer peripheral portion achieves high-temperature strength and the inner peripheral portion achieves high fatigue strength. The evening bin engine according to the present embodiment is manufactured using the turbine disk according to the present embodiment. As a result, it is possible to obtain Yuichi Binjinjin with excellent reliability during high-temperature operation. As a result, this turbine engine has higher heat resistance and durability against high temperature loads.

Claims

The scope of the claims

1. A disc material composed of a precipitation-strengthened Ni-based alloy, characterized by having a fine crystal part with a crystal grain size of 20 zm or less and a coarse crystal part with a crystal grain size of 70 to 130〃m. Disc material to do.

2. A disk material composed of an α-precipitation strengthened Ni-based alloy, where the α-phase precipitates at the crystal grain boundaries and the crystal grain size is 20 m or less. A disk material characterized by having coarse crystal parts having a crystal grain size of 70 to 130 µm without precipitation.

3. The disk material according to claim 1, wherein the fine crystal portion is an inner peripheral portion of the disk, and the coarse crystal portion is an outer peripheral portion of the disk.

4. 'Part of the constructed Dace click body § ⁵ precipitation strengthened N i based alloys reinforced precipitated by phase, §' § than dissolution temperature-dissolution temperature of phase 10 ° C higher temperature After the first heat treatment of heating for a short time in the range, the entire disc body is 100 ° C lower than the heating temperature of the first heat treatment to 10 ° C lower than the heating temperature of the first heat treatment. A second heat treatment of heating for a predetermined time in a temperature range is performed, and a part of the disk body is formed into a coarse crystal part having a crystal grain size of 70 to 130 m, and the remaining part of the disk body is formed with a crystal grain size of 20 zm or less. A method for producing a disk material, wherein the method comprises forming a disk material on a fine crystal part.

5. The method of manufacturing a disk material according to claim 4, wherein a part of the disk body is an outer peripheral portion of the disk, and a remaining portion of the disk body is an inner peripheral portion of the disk.

6. The method for producing a disk material according to claim 4, wherein a heating temperature of the first heat treatment is 1170 to 1200 ° C and a heating time is 0.1 to 2.0 hours.

7. The method for producing a disk material according to any one of claims 4 to 6, wherein the heating temperature of the second heat treatment is 1070 or more: U90 ° C, and the heating time is 0.5 to I0h.

8. The method according to claim 4, wherein the first heat treatment is performed by high-frequency induction heating.

9. The method for producing a disk material according to claim 4, wherein the first heat treatment is performed by salt bath immersion.

10. A turbine disk manufactured using the disk material according to claim 1.

11. A turbine engine manufactured using the turbine disk according to claim 10.