METHOD FOR REMOVING PRIOR PARTICLE BOUNDARY AND HOLE DEFECT OF POWDER METALLURGY HIGH-TEMPERATURE ALLOY

Abstract

A method for removing prior particle boundaries and hole defects of a powder metallurgy high-temperature alloy. The method includes performing mechanical ball milling treatment on an atomized powder, thermosetting the powder to form a shape, and preparing a powder metallurgy high-temperature alloy.

Claims

1. A method for removing prior particle boundaries and hole defects of a powder metallurgy high-temperature alloy, comprising: first performing mechanical ball milling treatment on high-temperature alloy powder prepared by using an atomization method to prepare surface activated solid powder, then thermosetting the powder to form a shape, and preparing a powder metallurgy high-temperature alloy.

2. The method for removing prior particle boundaries and hole defects of a powder metallurgy high-temperature alloy according to claim 1, wherein granularity of the atomized alloy powder is less than or equal to 150 μm.

3. The method for removing prior particle boundaries and hole defects of a powder metallurgy high-temperature alloy according to claim 1, wherein in ball milling, a used ball mill is one of a planetary ball mill, a stirring ball mill, and a roller drum ball mill.

4. The method for removing prior particle boundaries and hole defects of a powder metallurgy high-temperature alloy according to claim 3, wherein ball milling is performed under protection of an inert gas.

5. The method for removing prior particle boundaries and hole defects of a powder metallurgy high-temperature alloy according to claim 3, wherein atomized powder is put into a ball mill pot with a ball-to-powder ratio of: (8-12): 1, and ball milling is performed in a planetary ball mill for 1-4 h at a ball milling rotation speed of 250-350 r/min.

6. The method for removing prior particle boundaries and hole defects of a powder metallurgy high-temperature alloy according to claim 3, wherein atomized powder is put into a ball mill pot with a ball-to-powder ratio of: (8-15): 1, and ball milling is performed in a stirring ball mill for 2-6 h at a ball milling rotation speed of 60-150 r/min.

7. The method for removing prior particle boundaries and hole defects of a powder metallurgy high-temperature alloy according to claim 4, wherein thermosetting forming uses one forming manner of hot iso-hydrostatic forming, hot extrusion forming, and plasma sintering forming.

8. The method for removing prior particle boundaries and hole defects of a powder metallurgy high-temperature alloy according to claim 7, wherein a processing parameter of the hot iso-hydrostatic forming is 1000-1250° C./100-150 MPa/4 h; processing parameters of the hot extrusion forming are: performing hot extrusion forming at 900-1200° C.; an extrusion ratio of the hot extrusion forming is (6-15): 1; and a processing parameter of the plasma sintering forming is: 1000-1250° C./40-150 MPa/5-10 min.

9. The method for removing prior particle boundaries and hole defects of a powder metallurgy high-temperature alloy according to claim 8, wherein solution treatment and aging treatment are performed on a material of the high-temperature alloy formed by thermosetting.

10. The method for removing prior particle boundaries and hole defects of a powder metallurgy high-temperature alloy according to claim 9, wherein processing parameters of the solution treatment are: performing heat preservation for 1-2 h at 1000-1250° C., and performing air cooling; and processing parameters of the aging treatment are: performing heat preservation for 4-10 h at 700-900° C., and performing air cooling.

11. The method for removing prior particle boundaries and hole defects of a powder metallurgy high-temperature alloy according to claim 1, wherein thermosetting forming uses one forming manner of hot iso-hydrostatic forming, hot extrusion forming, and plasma sintering forming.

12. The method for removing prior particle boundaries and hole defects of a powder metallurgy high-temperature alloy according to claim 2, wherein thermosetting forming uses one forming manner of hot iso-hydrostatic forming, hot extrusion forming, and plasma sintering forming.

13. The method for removing prior particle boundaries and hole detects of a powder metallurgy high-temperature alloy according to claim 3, wherein thermosetting forming uses one forming mariner of hot iso-hydrostatic forming, hot extrusion forming, and plasma sintering forming.

14. The method for removing prior particle boundaries and hole defects of a powder metallurgy high-temperature alloy according to claim 5, wherein thermosetting forming uses one forming manner of hot iso-hydrostatic forming, hot extrusion forming, and plasma sintering forming.

15. The method for removing prior particle boundaries and hole defects of a powder metallurgy high-temperature alloy according to claim 6, wherein thermosetting forming uses one forming manner of hot iso-hydrostatic forming, hot extrusion forming, and plasma sintering forming.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0028] The accompanying drawings are included to provide a further understanding of the disclosure, and are incorporated in and constitute a part of this specification. The drawings illustrate embodiments of the disclosure and, together with the description, serve to explain the principles of the disclosure.

[0029] FIG. 1 is a metallographic microscopic structure of Rene 104 nickel-based high-temperature alloy prepared by performing plasma sintering forming on atomized nickel-based high-temperature alloy powder of a comparative example of the disclosure.

[0030] FIG. 2 is a scanning electronic microscope (SEM) diagram of a cross section of nickel-based high-temperature alloy atomized powder in embodiment 1 of the disclosure.

[0031] FIG. 3 is an SEM diagram of a cross section of powder after mechanical ball milling is performed on nickel-based high-temperature alloy atomized powder in embodiment 1 of the disclosure.

[0032] FIG. 4 is a metallographic microscopic structure of Rene 104 nickel-based high-temperature alloy prepared by performing plasma sintering forming after mechanical ball milling is performed on atomized nickel-based high-temperature alloy powder in embodiment 1 of the disclosure.

[0033] According to a metallographic observation result of FIG. 1, obvious prior particle boundaries (PPB) occur to microscopic structures of the nickel-based high-temperature alloy prepared by directly forming atomized powder, and 1 and 2 in FIG. 1 both indicate prior particle boundaries.

[0034] According to an SEM observation result of FIG. 2, obvious hollow defects occur to some atomized powder in embodiment 1, and parts 3, 4, 5, and 6 in FIG. 2 are all hollow defects.

[0035] According to an SEM observation result of FIG. 3, after mechanical ball milling is performed on atomized powder in embodiment 1, no hollow phenomenon is observed on a cross section of powder.

[0036] According to an observation result of an optical microscope of FIG. 4, no obvious prior particle boundaries are observed on microscopic structures of the nickel-based high-temperature alloy prepared in embodiment 1.

DESCRIPTION OF THE EMBODIMENTS

[0037] Reference will now be made in detail to the present preferred embodiments of the disclosure, examples of which are illustrated in the accompanying drawings.

[0038] Wherever possible, the same reference numbers are used in the drawings and the description to refer to the same or like parts.

[0039] The disclosure is further described below with reference to specific embodiments.

[0040] Comparative example: direct plasma sintering is performed on atomized powder to prepare Rene 104 nickel-based high-temperature alloy.

[0041] Plasma sintering is performed on gas atomized Rene 104 nickel-based pre-alloyed powder (components are Ni-13Co-16Cr-4Mo-4W-2.2Al-3.7Ti-0.77Nb (wt %)); processing parameters are: 1150° C./40 MPa/heat preservation for 5 min, and then solution treatment is performed; the solution treatment is performed at 1180° C. for 1 h, and furnace cooling is performed; and then aging treatment s performed at 815° C. for 8 h to obtain a nickel-based high-temperature alloy.

[0042] FIG. 1 is a microscopic structure of Rene 104 nickel-based high-temperature alloy prepared in this comparative example, and obvious prior particle boundaries can be observed. See parts indicated by 1 and 2 in FIG. 1.

Embodiment 1

[0043] Gas atomized Rene 104 nickel-based pre-alloyed powder is put into a ball mill pot with a ball-to-powder ratio of 10:1, and ball milling is performed in a planetary ball mill for 1.5 h at a ball milling rotation speed of 250 r/min under protection of argon, to obtain ball milling nickel-based high-temperature alloy powder.

[0044] Plasma sintering is performed on ball milling nickel-based high-temperature alloy powder at 1150° C./40 MPa, and heat preservation is performed for 5 min, then solution treatment is performed; the solution treatment is performed at 1180° C. for 1 h, and furnace cooling is performed; then, aging treatment is performed at 815° C. for 8 h to obtain a nickel-based high-temperature alloy.

[0045] FIG. 2 is a scanning electronic microscope (SEM) diagram of a cross section of atomized powder of the present embodiment, and obvious hollow defects occur to some powder in FIG. 2. See parts indicated by 3, 4, 5, and 6 in FIG. 2. FIG. 3 is an SEM diagram of a cross section of powder after mechanical ball milling is performed on atomized powder in the present embodiment, and no powder hollow phenomenon is observed. FIG. 4 is a metallographic microscopic structure of a nickel-based powder high-temperature alloy prepared in the present embodiment, and no obvious prior particle boundaries are observed.

Embodiment 2

[0046] Gas atomized Rene 104 nickel-based pre-alloyed powder is put into a ball mill pot, and ball milling is performed in a stirring ball mill for 3 h at a ball milling rotation speed of 100 r/min under protection of argon, to obtain ball milling nickel-based high-temperature alloy powder.

[0047] Ball milling powder is put into a steel capsule; vacuuming and sealing welding are performed on the steel capsule; hot extrusion forming is performed at 1100° C. with an extrusion ratio of 10:1 to obtain a highly compact nickel-based alloy bar; finally, solution treatment is performed at 1115° C. for 1 h and performed at 1170° C. for 3 h and air cooling is performed; aging treatment is performed at 845° C. for 4 h and performed at 760° C. for 8 h and air cooling is performed, to obtain a nickel-based high-temperature alloy.

[0048] It will be apparent to those skilled in the art that various modifications and variations can be made to the structure of the present disclosure without departing from the scope or spirit of the disclosure. In view of the foregoing, it is intended that the present disclosure cover modifications and variations of this disclosure provided they fall within the scope of the following claims and their equivalents.