CN113118420A - Superfine columnar crystal high-temperature alloy blade and laser directional solidification preparation method thereof - Google Patents
Superfine columnar crystal high-temperature alloy blade and laser directional solidification preparation method thereof Download PDFInfo
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- CN113118420A CN113118420A CN202110679251.7A CN202110679251A CN113118420A CN 113118420 A CN113118420 A CN 113118420A CN 202110679251 A CN202110679251 A CN 202110679251A CN 113118420 A CN113118420 A CN 113118420A
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- 239000013078 crystal Substances 0.000 title claims abstract description 44
- 238000007711 solidification Methods 0.000 title claims abstract description 38
- 230000008023 solidification Effects 0.000 title claims abstract description 38
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 28
- 239000000956 alloy Substances 0.000 title claims abstract description 28
- 238000002360 preparation method Methods 0.000 title abstract description 10
- 238000000034 method Methods 0.000 claims abstract description 29
- 239000000758 substrate Substances 0.000 claims abstract description 28
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 27
- 229910052802 copper Inorganic materials 0.000 claims abstract description 27
- 239000010949 copper Substances 0.000 claims abstract description 27
- 230000008021 deposition Effects 0.000 claims abstract description 21
- 239000000498 cooling water Substances 0.000 claims abstract description 4
- 239000000843 powder Substances 0.000 claims description 18
- 238000010438 heat treatment Methods 0.000 claims description 14
- 229910000601 superalloy Inorganic materials 0.000 claims description 8
- 239000000203 mixture Substances 0.000 claims description 5
- 239000000463 material Substances 0.000 claims description 4
- 238000012544 monitoring process Methods 0.000 claims description 4
- 239000000155 melt Substances 0.000 claims 1
- 238000001816 cooling Methods 0.000 description 26
- 239000010410 layer Substances 0.000 description 13
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 12
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 4
- 238000005137 deposition process Methods 0.000 description 4
- 230000017525 heat dissipation Effects 0.000 description 4
- 239000002826 coolant Substances 0.000 description 3
- 210000001787 dendrite Anatomy 0.000 description 3
- 239000006185 dispersion Substances 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 2
- 229910052786 argon Inorganic materials 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 238000005192 partition Methods 0.000 description 2
- 239000012071 phase Substances 0.000 description 2
- 238000005498 polishing Methods 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- 244000137852 Petrea volubilis Species 0.000 description 1
- 238000013459 approach Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000007713 directional crystallization Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 238000011049 filling Methods 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 238000011065 in-situ storage Methods 0.000 description 1
- 239000011229 interlayer Substances 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 229910001338 liquidmetal Inorganic materials 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 238000007712 rapid solidification Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D27/00—Treating the metal in the mould while it is molten or ductile ; Pressure or vacuum casting
- B22D27/04—Influencing the temperature of the metal, e.g. by heating or cooling the mould
- B22D27/045—Directionally solidified castings
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22C—FOUNDRY MOULDING
- B22C9/00—Moulds or cores; Moulding processes
- B22C9/22—Moulds for peculiarly-shaped castings
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D46/00—Controlling, supervising, not restricted to casting covered by a single main group, e.g. for safety reasons
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- Crystals, And After-Treatments Of Crystals (AREA)
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Abstract
The invention discloses a laser directional solidification preparation method of an ultrafine columnar crystal high-temperature alloy blade, which specifically comprises the following steps: 1) placing a substrate on a water-cooled copper plate, enabling the substrate to be vertical to the water-cooled copper plate in the <001> orientation, wherein the water-cooled copper plate is movably arranged in a water-cooled box, and cooling water is filled in the space below the water-cooled copper plate of the water-cooled box and the periphery of the water-cooled box; 2) and carrying out directional solidification deposition by adopting a laser layer-by-layer scanning mode to prepare the columnar crystal, wherein in the scanning process, a scanning mode that the layers are not overlapped and are overlapped is adopted, and the water-cooled copper plate moves downwards along the inner wall of the water-cooled box after each layer of scanning is finished. The laser directional solidification preparation method can maintain a stable ultrahigh directional temperature gradient in a large range and maintain the integral orientation of integral columnar crystals.
Description
Technical Field
The invention relates to the technical field of laser directional solidification, in particular to an ultrafine columnar crystal high-temperature alloy blade and a laser directional solidification preparation method thereof.
Background
The performance of an engine blade is one of the important factors that limit the performance level of an aircraft engine, and the blade is generally required to be capable of stable operation at high temperature and high pressure for a long time. And the grain boundary of the vertical stress axis becomes a weak part of the common cast high-temperature alloy, so that the high-temperature alloy generates creep fracture at a small deformation amount at high temperature. The directional crystallization blade eliminates transverse crystal boundaries sensitive to cavities and cracks, and all the crystal boundaries are parallel to the stress axis direction, so that the service performance of the alloy can be improved.
The traditional casting directional solidification technology such as a power reduction method, a liquid metal cooling method and the like has small temperature gradient, low solidification cooling speed, large directional solidification columnar crystal structure, loose dendrites and serious solidification segregation of alloy elements, so that uniform and consistent directional structures are difficult to obtain, the superiority on the mechanical property of the columnar crystals can be displayed to the maximum extent only when the main stress direction is consistent with the columnar crystal growth direction, and the high-temperature mechanical property is rapidly reduced when the columnar crystal growth direction deviates from the main stress axis. Therefore, the degree of orientation dispersion is not more than 10 ° when the blade is produced.
The laser directional solidification technology provides a new technical approach for breaking through the bottleneck. Important process parameters of the directional solidification technology are mainly the temperature gradient in the liquid phase at the front edge in the solidification process and the cooling speed. The ultra-high temperature gradient and the rapid solidification cooling in the deposition process of the laser melting deposition technology can meet the requirement of the directional solidification of the epitaxial growth of the columnar crystal, and can also reduce the segregation.
However, during the layer-by-layer deposition process of laser directional solidification, the columnar crystal may deviate from the central position due to the influence of the surface tension of the molten pool liquid and the strong internal convection. Although many researches and achievements exist for the directional solidification of columnar crystals at present, no very effective solution is provided for the problems, so that the product performance of the superfine directional columnar crystals prepared by the laser directional solidification is seriously influenced, and the application of the laser directional solidification technology in the preparation of the superfine columnar crystal high-temperature alloy blades is restricted.
Disclosure of Invention
According to the traditional high-temperature alloy HRS technology, the height of a solidified phase is continuously increased along with the proceeding of a directional solidification process, the cooling effect of a bottom water-cooling copper plate is gradually reduced, and the temperature gradient is reduced, so that the dispersion and the non-uniform structure of columnar crystals are caused, and the problems of thick columnar crystals and columnar crystals with large orientation degree in a directional solidification blade are caused.
The invention aims to provide a method for preparing an ultrafine columnar crystal high-temperature alloy blade through laser directional solidification, so as to solve the problems.
The technical scheme of the invention is a method for preparing an ultrafine columnar crystal high-temperature alloy blade by laser directional solidification, which comprises the following steps:
1) placing a substrate on a water-cooled copper plate, and enabling the <001> orientation of the substrate to be consistent with the normal direction of the water-cooled copper plate, wherein the water-cooled copper plate is movably arranged in a water-cooled box, and the space below the water-cooled copper plate of the water-cooled box and the periphery of the water-cooled box are filled with cooling water;
2) and carrying out directional solidification deposition by adopting a laser layer-by-layer scanning mode to prepare the columnar crystal, wherein in the scanning process, a scanning mode that the layers are not overlapped and are overlapped is adopted, and the water-cooled copper plate moves downwards along the inner wall of the water-cooled box after each layer of scanning is finished.
Further preferably, the stroke Z of the downward movement is
，
Wherein d is the diameter of a light spot, v is the scanning speed, g is the powder feeding amount, rho is the material density, k is the empirical coefficient generated by the influence of the shape of a molten pool and the solidification process on the shape of a deposition layer, and is 1.5-1.7, and r is the lap joint rate which is 30-35%.
Preferably, a resistance wire is adopted to perform auxiliary heating above the molten pool while laser scanning deposition is performed.
Preferably, the temperature around the molten pool is monitored by an infrared camera, and the resistance wire is controlled to perform auxiliary heating according to the monitoring result so as to adjust the temperature around the molten pool to be consistent with the preset temperature.
Further preferably, the preset temperature T is,
wherein W is the laser power, V is the scanning speed, and G is the powder feeding speed. Wherein alpha, beta and epsilon are alloy composition parameters, and C is a temperature compensation coefficient.
Preferably, the substrate is a high-temperature alloy substrate subjected to laser directional deposition, the high-temperature alloy and the superfine columnar crystal high-temperature alloy blade have the same components, and the substrate is subjected to solution treatment.
More preferably, the substrate is a DZ408 substrate, the substrate orientation is <001> orientation, spherical alloy powder for laser forming of DZ408 high-temperature alloy is adopted for laser scanning deposition, and the diameter of the powder is 30-50 μm.
Preferably, the laser power of the laser scanning deposition is 3000-4000W, the beam spot diameter is 4-6 mm, the scanning speed is 500-800 mm/min, and the powder feeding amount is 3-5 g/min.
More preferably, the auxiliary heating power is 1500-2000W.
Meanwhile, the invention also provides an ultrafine columnar crystal high-temperature alloy blade which is prepared by adopting the laser directional solidification preparation method.
Compared with the prior art, the invention has the beneficial effects that:
the invention designs and prepares an ultrafine columnar crystal high-temperature alloy blade based on a laser directional solidification method.
First, make base plate bottom forced cooling, keep the whole decurrent heat dissipation direction of deposit blade all the time to at the in-process of scanning deposit, control water-cooling copper plate successive layer moves down, combines to use unique cooling water tank, thereby makes the water-cooling contact that the base plate can be abundant, consequently can maintain a stable super high directional temperature gradient in very big range, keeps whole columnar crystal whole orientation.
Secondly, as laser deposition is a process of stacking countless molten pools, convection in a single molten pool is reasonably controlled, and the temperature gradient around the single molten pool is controlled in order to maintain the shape and the size of the molten pool to be constant, two resistance wire auxiliary heating devices are additionally arranged above the molten pool, the form change of the molten pool is reduced, the temperature gradient around the molten pool is reduced, and the ultrahigh temperature gradient in the crystal orientation direction only exists, and an infrared camera is used for controlling auxiliary heating, so that the form change of the molten pool is reduced, the temperature gradient around the molten pool is reduced, and the ultrahigh temperature gradient in the crystal orientation direction only exists.
Thirdly, the scanning deposition mode of not lapping in layers but lapping among layers is adopted, so that the defects of porosity and the like are ensured to be reduced, and the disordered orientation crystal grains in the lapping area of a molten pool can be well reduced.
Fourthly, by controlling the downward movement stroke of the water-cooled copper plate, the optimal interlaminar lap joint rate is obtained, and uniform and defect-free tissues are obtained.
Fifthly, the temperature of the molten pool is controlled through accurate empirical calculation of the preset temperature, so that the optimal auxiliary heating effect is obtained.
Drawings
FIG. 1 is a schematic view of a special apparatus for implementing the laser directional solidification preparation method of the present invention.
FIG. 2 is a schematic view of laser scanning deposited interlayer lap joint according to the present invention.
FIG. 3 is a structural photograph of the ultra-fine columnar crystal superalloy blade manufactured by the present invention.
Detailed Description
The technical solutions in the embodiments of the present invention will be described below with reference to the drawings in the embodiments of the present invention.
Example 1
A special device for implementing the laser directional solidification preparation method. The preparation method of the invention is carried out by a special device self-developed by an inventor, as shown in figure 1, the special device comprises a processing chamber 1, a partition plate 2 is arranged in the middle of the processing chamber 1, an opening is arranged in the middle of the partition plate, a water cooling tank 3 is arranged downwards along the opening, a water cooling copper plate 4 is arranged on the upper part of the water cooling tank 3, a channel is arranged at the bottom of the water cooling tank 3, so that a cooling medium can enter a space of the water cooling tank 3, which is positioned below the water cooling copper plate 4, a directional solidification substrate 5 is arranged on the water cooling copper plate 4, an upper driving device 6 and a lower driving device 6 are fixedly connected to the bottom surface of the water cooling copper plate 4, the driving device 6 is connected with a power mechanism 7 arranged outside the processing chamber 1 to realize the up-down. During the use, place directional solidification base plate 5 on water-cooling copper 4 for the orientation of directional solidification base plate 5 is perpendicular with the surface of water-cooling copper 4, open argon gas filling equipment 8 so that be full of the protection argon gas in handling cavity 1, let in cooling medium simultaneously and make cooling medium fill the space that is located the below water-cooling copper 4 of water-cooling tank 3, later start laser instrument 9 and open powder feeder 10 and carry out laser scanning deposition, in order to deposit superfine column crystal superalloy blade 11, in the scanning deposition process, simultaneously open resistance wire 12 and carry out the auxiliary heating, and open infrared camera 13 and monitor the molten bath temperature, control resistance wire 12 according to monitoring temperature and the relation of presetting the temperature and heat. In order to keep the directional solidification substrate 5 stable and better cool heat dissipation, a jig 14 is provided between the inner wall of the water cooling tank 3 and the directional solidification substrate 5, wherein the water cooling tank 3 and the jig 14 are also preferably made of copper material with good thermal conductivity.
And (4) selecting a substrate. The laser directional deposition of the homoconstituent DZ408 substrate with the <001> orientation is selected, XRD can be used for detecting whether the substrate orientation is the <001> orientation, and in order to prevent heterogeneous nucleation from hindering the epitaxial growth of columnar crystals, the substrate is subjected to solution treatment of homoconstituent DZ408 high-temperature alloy at 1230 ℃ multiplied by 2h +1260 ℃ multiplied by 2 h/air cooling in advance. And then polishing with fine sand paper to keep the substrate flat, and cleaning with ethanol and drying.
And (4) selecting powder. The special spherical alloy powder for DZ408 high-temperature alloy laser forming is selected, the diameter of the powder is 30-50 mu m, and the powder is dried in vacuum at 200 ℃ and is kept warm to remove water. The mass fraction% of the chemical components is shown in the following table 1:
TABLE 1 DZ408 superalloy chemical composition parts by mass (%)
| C | Co | Cr | Mo | Ti | W | Al | Ta | Hf | Ni |
| 0.086 | 8.97 | 8.03 | 0.50 | 0.66 | 9.34 | 5.51 | 3.28 | 1.46 | Bal. |
Laser scanning the process parameters of deposition. The laser power is 3500W, the beam spot diameter is 5mm, the scanning speed is 600mm/min, and the powder feeding speed is 4 g/min.
The scanning mode. Because the transverse lapping mode is adopted during forming the part, disordered oriented crystal grains can appear on the tissues of the lapping part, and therefore, as shown in figure 2, a scanning mode that the layers are not lapped and are lapped is selected.
Because the layers are not overlapped, the descending amount of the deposition blade is reasonably controlled by the downward moving stroke of the water-cooling copper plate, and the layers are fully melted by adopting small descending amount without generating new crystal nucleus. The descending amount Z is mainly used for controlling the overlapping rate, good combination between layers can be ensured only by the large enough overlapping rate, but new crystal nuclei can be generated due to the large enough overlapping rate, and the growth of the superfine columnar crystals is influenced. The amount of decrease Z is given by the following empirical formula:
wherein d is the diameter of a light spot, v is the scanning speed, g is the powder feeding amount, rho is the density of the material, and the density of the DZ408 high-temperature alloy is 8.63
10-3g/mm3K is an empirical coefficient generated by the influence of the shape of a molten pool and the solidification process on the shape of a deposition layer, and is 1.5-1.7, r is an overlap ratio which is 30-35%, in the embodiment, k is 1.6, r is 33%, and Z =0.2mm is obtained through calculation.
Determination of auxiliary heating power. The auxiliary heating power is to ensure that the temperature of the laser molten pool is consistent with the preset temperature all the time, wherein the temperature of the laser molten pool is obtained by monitoring the ambient temperature of the molten pool by the infrared camera 13, the preset temperature T is generated by adopting data computer fitting of a plurality of tests, in particular to carry out multivariate linear fitting in matlab software, the inventor selects a plurality of function models, and the correlation of T obtained by calculating the following function models is the best through repeated groping tests,
wherein W is the laser power, V is the scanning speed, and G is the powder feeding speed. Wherein α, β, and ∈ are alloy composition parameters, and for the process parameters of this embodiment, α =0.432, β = -0.0795, and ∈ =0.3492 are taken, C is a temperature compensation coefficient, and C = 67.817. According to the formula, the process parameters are controlled, and the temperature of the molten pool is controlled to be 2200-2300 ℃.
The temperature distribution range around the molten pool is analyzed through the infrared camera 13, the power of the auxiliary heating resistance wire is further adjusted, the periphery of the molten pool is heated in situ, the heat dissipation direction of the molten pool is forced to dissipate heat towards the bottom, and the power can be between 1500W and 2000W.
And finally, cutting, grinding, polishing and corroding the real object, and observing the growth condition of the superfine columnar crystal under a metallographic phase. As can be seen from FIG. 3, the ultrafine columnar crystals prepared by the present invention have very small degree of orientation dispersion, are fine dense columnar crystals epitaxially grown from a substrate, have a primary dendrite spacing of about 6 to 11 μm, and have almost no secondary dendrite arms.
Therefore, the bottom of the substrate is forcibly cooled by the invention, and the whole deposition blade is always kept in the downward heat dissipation direction. Sufficient water cooling contact can maintain a stable ultrahigh directional temperature gradient in a large range and maintain the whole columnar crystal to be in a <001> orientation. Two resistance wire auxiliary heating devices are added above the molten pool, so that the form change of the molten pool is reduced, and the temperature gradient around the molten pool is reduced, so that the ultrahigh temperature gradient in the (001) direction only exists. The method for obtaining the superfine oriented columnar crystal superalloy blade by controlling the orientation and the ultrahigh temperature gradient in the laser deposition process is feasible.
The above description is only for the preferred embodiment of the present invention, but the scope of the present invention is not limited thereto, and any changes or substitutions that can be easily conceived by those skilled in the art within the technical scope of the present invention are included in the scope of the present invention. Therefore, the protection scope of the present invention shall be subject to the protection scope of the appended claims.
Claims (10)
1. A method for preparing an ultrafine columnar crystal high-temperature alloy blade through laser directional solidification specifically comprises the following steps:
1) placing a substrate on a water-cooled copper plate, wherein the orientation <001> of the substrate is perpendicular to the water-cooled copper plate, the water-cooled copper plate is movably arranged in a water-cooled box, and the space below the water-cooled copper plate of the water-cooled box and the periphery of the water-cooled box are filled with cooling water;
2) and carrying out directional solidification deposition by adopting a laser layer-by-layer scanning mode to prepare the columnar crystal, wherein in the scanning process, a scanning mode that the layers are not overlapped and are overlapped is adopted, and the water-cooled copper plate moves downwards along the inner wall of the water-cooled box after each layer of scanning is finished.
2. The method of claim 1, wherein the stroke Z of the downward movement is
，
Wherein d is the diameter of a light spot, v is the scanning speed, g is the powder feeding amount, rho is the material density, k is the empirical coefficient generated by the influence of the shape of a molten pool and the solidification process on the shape of a deposition layer, and is 1.5-1.7, and r is the lap joint rate which is 30-35%.
3. The method as claimed in claim 1, characterized in that, while the laser scanning deposition is being carried out, an auxiliary heating is carried out above the bath using a resistance wire.
4. The method as claimed in claim 3, wherein the temperature around the molten pool is monitored by an infrared camera, and the resistance wire is controlled to perform auxiliary heating according to the monitoring result so as to ensure the stability and directionality of the temperature of the molten pool.
5. The method according to claim 4, characterized in that the melt pool temperature T is,
wherein W is laser power, V is scanning speed, G is powder feeding speed, wherein alpha, beta and epsilon are alloy composition parameters, and C is temperature compensation coefficient.
6. The method of claim 1, wherein the substrate is a laser directionally deposited superalloy substrate having the same composition as the ultra-fine columnar superalloy blade, and the substrate is solution treated.
7. The method of claim 1, wherein the substrate is a DZ408 substrate, the substrate orientation is a <001> orientation, and the laser scanning deposition uses a spherical alloy powder for DZ408 superalloy laser forming, the powder diameter being 30-50 μm.
8. The method of claim 3, wherein the laser power of the laser scanning deposition is 3000-4000W, the beam spot diameter is 4-6 mm, the scanning speed is 500-800 mm/min, and the powder feeding amount is 3-5 g/min.
9. The method according to claim 3, wherein the auxiliary heating power is 1500-2000W.
10. An ultra-fine columnar grain superalloy blade produced by the method of any of claims 1 to 9.
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| CN114150367A (en) * | 2021-11-26 | 2022-03-08 | 华中科技大学 | Laser cladding repair method and repair system for high-temperature alloy single crystal defects |
| CN114309659A (en) * | 2021-11-19 | 2022-04-12 | 中国航发北京航空材料研究院 | High-temperature alloy laser rapid forming system and forming method |
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