CN110483087A - Turbine blade of gas turbine hot investment casting alumina based ceramic core manufacturing method - Google Patents
Turbine blade of gas turbine hot investment casting alumina based ceramic core manufacturing method Download PDFInfo
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- 239000000919 ceramic Substances 0.000 title claims abstract description 124
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 title claims abstract description 52
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 30
- 238000005495 investment casting Methods 0.000 title claims abstract description 18
- 239000011347 resin Substances 0.000 claims abstract description 111
- 229920005989 resin Polymers 0.000 claims abstract description 111
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 claims abstract description 53
- 238000000034 method Methods 0.000 claims abstract description 31
- 239000002002 slurry Substances 0.000 claims abstract description 27
- KZHJGOXRZJKJNY-UHFFFAOYSA-N dioxosilane;oxo(oxoalumanyloxy)alumane Chemical group O=[Si]=O.O=[Si]=O.O=[Al]O[Al]=O.O=[Al]O[Al]=O.O=[Al]O[Al]=O KZHJGOXRZJKJNY-UHFFFAOYSA-N 0.000 claims abstract description 26
- 229910052863 mullite Inorganic materials 0.000 claims abstract description 26
- 239000000377 silicon dioxide Substances 0.000 claims abstract description 23
- 238000005245 sintering Methods 0.000 claims abstract description 21
- 238000005238 degreasing Methods 0.000 claims abstract description 16
- 239000007788 liquid Substances 0.000 claims abstract description 16
- 230000008569 process Effects 0.000 claims abstract description 13
- 230000002194 synthesizing effect Effects 0.000 claims abstract description 13
- 235000015895 biscuits Nutrition 0.000 claims abstract description 11
- 238000001746 injection moulding Methods 0.000 claims abstract description 8
- 230000015572 biosynthetic process Effects 0.000 claims abstract description 6
- 238000007598 dipping method Methods 0.000 claims abstract description 6
- 238000011065 in-situ storage Methods 0.000 claims abstract description 6
- 238000003786 synthesis reaction Methods 0.000 claims abstract description 3
- 239000000463 material Substances 0.000 claims description 71
- 239000000843 powder Substances 0.000 claims description 38
- 238000010792 warming Methods 0.000 claims description 24
- 239000007789 gas Substances 0.000 claims description 22
- 239000000243 solution Substances 0.000 claims description 19
- 239000003431 cross linking reagent Substances 0.000 claims description 15
- 239000000178 monomer Substances 0.000 claims description 14
- IRPGOXJVTQTAAN-UHFFFAOYSA-N 2,2,3,3,3-pentafluoropropanal Chemical compound FC(F)(F)C(F)(F)C=O IRPGOXJVTQTAAN-UHFFFAOYSA-N 0.000 claims description 11
- KLZUFWVZNOTSEM-UHFFFAOYSA-K Aluminum fluoride Inorganic materials F[Al](F)F KLZUFWVZNOTSEM-UHFFFAOYSA-K 0.000 claims description 11
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Chemical compound O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 11
- 239000013078 crystal Substances 0.000 claims description 10
- 239000008367 deionised water Substances 0.000 claims description 10
- 229910021641 deionized water Inorganic materials 0.000 claims description 10
- 238000010438 heat treatment Methods 0.000 claims description 9
- ROOXNKNUYICQNP-UHFFFAOYSA-N ammonium persulfate Chemical group [NH4+].[NH4+].[O-]S(=O)(=O)OOS([O-])(=O)=O ROOXNKNUYICQNP-UHFFFAOYSA-N 0.000 claims description 8
- 239000002270 dispersing agent Substances 0.000 claims description 8
- 238000000465 moulding Methods 0.000 claims description 8
- 229910052782 aluminium Inorganic materials 0.000 claims description 7
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 7
- 239000007864 aqueous solution Substances 0.000 claims description 7
- 229910052814 silicon oxide Inorganic materials 0.000 claims description 7
- 239000003054 catalyst Substances 0.000 claims description 6
- 229910052593 corundum Inorganic materials 0.000 claims description 6
- 239000003999 initiator Substances 0.000 claims description 6
- 239000000203 mixture Substances 0.000 claims description 6
- 239000007790 solid phase Substances 0.000 claims description 6
- 239000004411 aluminium Substances 0.000 claims description 5
- 239000010431 corundum Substances 0.000 claims description 5
- 238000004321 preservation Methods 0.000 claims description 5
- HRPVXLWXLXDGHG-UHFFFAOYSA-N Acrylamide Chemical group NC(=O)C=C HRPVXLWXLXDGHG-UHFFFAOYSA-N 0.000 claims description 4
- KWYHDKDOAIKMQN-UHFFFAOYSA-N N,N,N',N'-tetramethylethylenediamine Chemical compound CN(C)CCN(C)C KWYHDKDOAIKMQN-UHFFFAOYSA-N 0.000 claims description 4
- 229910001870 ammonium persulfate Inorganic materials 0.000 claims description 4
- 238000004090 dissolution Methods 0.000 claims description 3
- ZIUHHBKFKCYYJD-UHFFFAOYSA-N n,n'-methylenebisacrylamide Chemical compound C=CC(=O)NCNC(=O)C=C ZIUHHBKFKCYYJD-UHFFFAOYSA-N 0.000 claims description 3
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 claims description 3
- 229920001495 poly(sodium acrylate) polymer Polymers 0.000 claims description 3
- NNMHYFLPFNGQFZ-UHFFFAOYSA-M sodium polyacrylate Chemical compound [Na+].[O-]C(=O)C=C NNMHYFLPFNGQFZ-UHFFFAOYSA-M 0.000 claims description 3
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 2
- 229910052760 oxygen Inorganic materials 0.000 claims description 2
- 239000001301 oxygen Substances 0.000 claims description 2
- 238000007493 shaping process Methods 0.000 claims description 2
- 229910052571 earthenware Inorganic materials 0.000 claims 1
- 239000011162 core material Substances 0.000 abstract description 153
- 238000005266 casting Methods 0.000 abstract description 7
- 230000007812 deficiency Effects 0.000 abstract description 2
- 230000004992 fission Effects 0.000 description 9
- 230000003647 oxidation Effects 0.000 description 7
- 238000007254 oxidation reaction Methods 0.000 description 7
- 239000011159 matrix material Substances 0.000 description 5
- 239000005416 organic matter Substances 0.000 description 5
- 238000010586 diagram Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 3
- 239000000835 fiber Substances 0.000 description 3
- 238000010574 gas phase reaction Methods 0.000 description 3
- 238000002156 mixing Methods 0.000 description 3
- 229910052710 silicon Inorganic materials 0.000 description 3
- 239000010703 silicon Substances 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 2
- 238000005470 impregnation Methods 0.000 description 2
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 239000005543 nano-size silicon particle Substances 0.000 description 2
- 239000012071 phase Substances 0.000 description 2
- 238000004382 potting Methods 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 238000000498 ball milling Methods 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 210000000746 body region Anatomy 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 229910052681 coesite Inorganic materials 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 239000002826 coolant Substances 0.000 description 1
- 229910052906 cristobalite Inorganic materials 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000011049 filling Methods 0.000 description 1
- 239000003292 glue Substances 0.000 description 1
- 230000005484 gravity Effects 0.000 description 1
- 229910001338 liquidmetal Inorganic materials 0.000 description 1
- 230000010412 perfusion Effects 0.000 description 1
- 229910052573 porcelain Inorganic materials 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 230000009257 reactivity Effects 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 239000011226 reinforced ceramic Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 238000003756 stirring Methods 0.000 description 1
- 229910052682 stishovite Inorganic materials 0.000 description 1
- 239000004575 stone Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 230000008646 thermal stress Effects 0.000 description 1
- 229910052905 tridymite Inorganic materials 0.000 description 1
- 229910001845 yogo sapphire Inorganic materials 0.000 description 1
Classifications
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- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/01—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics
- C04B35/10—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on aluminium oxide
- C04B35/101—Refractories from grain sized mixtures
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- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
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- C04B38/00—Porous mortars, concrete, artificial stone or ceramic ware; Preparation thereof
- C04B38/0003—Porous mortars, concrete, artificial stone or ceramic ware; Preparation thereof containing continuous channels, e.g. of the "dead-end" type or obtained by pushing bars in the green ceramic product
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- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2111/00—Mortars, concrete or artificial stone or mixtures to prepare them, characterised by specific function, property or use
- C04B2111/00474—Uses not provided for elsewhere in C04B2111/00
- C04B2111/00939—Uses not provided for elsewhere in C04B2111/00 for the fabrication of moulds or cores
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- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/34—Non-metal oxides, non-metal mixed oxides, or salts thereof that form the non-metal oxides upon heating, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3418—Silicon oxide, silicic acids, or oxide forming salts thereof, e.g. silica sol, fused silica, silica fume, cristobalite, quartz or flint
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- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
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- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/44—Metal salt constituents or additives chosen for the nature of the anions, e.g. hydrides or acetylacetonate
- C04B2235/444—Halide containing anions, e.g. bromide, iodate, chlorite
- C04B2235/445—Fluoride containing anions, e.g. fluosilicate
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- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
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- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/50—Constituents or additives of the starting mixture chosen for their shape or used because of their shape or their physical appearance
- C04B2235/52—Constituents or additives characterised by their shapes
- C04B2235/5208—Fibers
- C04B2235/5216—Inorganic
- C04B2235/522—Oxidic
- C04B2235/5228—Silica and alumina, including aluminosilicates, e.g. mullite
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- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/50—Constituents or additives of the starting mixture chosen for their shape or used because of their shape or their physical appearance
- C04B2235/52—Constituents or additives characterised by their shapes
- C04B2235/5276—Whiskers, spindles, needles or pins
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- C04B2235/50—Constituents or additives of the starting mixture chosen for their shape or used because of their shape or their physical appearance
- C04B2235/54—Particle size related information
- C04B2235/5418—Particle size related information expressed by the size of the particles or aggregates thereof
- C04B2235/5436—Particle size related information expressed by the size of the particles or aggregates thereof micrometer sized, i.e. from 1 to 100 micron
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- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/65—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes
- C04B2235/656—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes characterised by specific heating conditions during heat treatment
- C04B2235/6562—Heating rate
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- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/65—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes
- C04B2235/656—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes characterised by specific heating conditions during heat treatment
- C04B2235/6567—Treatment time
Abstract
The present invention relates to turbine blade of gas turbine hot investment casting alumina based ceramic core manufacturing method, the problem of depoling difficulty after the disconnected core and core shift problem and blade that effective solution large scale gas turbine blades casting process medium-sized core mechanical behavior under high temperature deficiency occurs are cast；Including step 1: step 2: production resin die prepares ceramic slurry, step 3: preparing ceramic core biscuit；Step 4: pre-burning degreasing；Step 5: high temperature sintering；Step 6: silica solution dipping is carried out to the ceramic core after synthesizing whisker, obtain secondary mullite, the present invention prepares the ceramic core of the structure containing inner flow passage by stereolithography and gel injection-moulding method, to depoling liquid be made to enter type core inner by runner during the core removal process, type core both ends and inside can be contacted with depoling liquid simultaneously, to increase the removing rate of core material, simultaneously, the On In-situ Synthesis of Mullite Whisker in type core improves the mechanical behavior under high temperature of type core.
Description
Technical field
The present invention relates to melted module precise casting technology fields, specifically turbine blade of gas turbine hot investment casting aluminium oxide
Base ceramic core manufacturing method.
Background technique
Hollow turbine vane is the kernel component of aero-engine and gas turbine, internal to contain complicated coolant flow channel
Structure.Currently, blade is mainly shaped by investment casting method, wherein ceramic core manufacture is the main ring of blade model casting
One of section.For large scale gas turbine blades, type core needs the long period to be maintained at high temperature in blade directional solidification process
In molten metal, it is easy disconnected core, core shift situation occur under molten metal gravity and thermal stress effect, causes vane manufacturing unqualified.
Therefore, the mechanical behavior under high temperature that type core needs to have excellent.
Currently, the main silica of core material and two kinds of aluminium oxide, wherein aluminium oxide has excellent change at high temperature
Learn stability, it is not easy to chemically react with high-temperature liquid metal, thus be gradually used widely, still, aluminium oxide with take off
The reactivity of core liquid is poor, causes blade cast form rear profile core removing difficulty big.In addition, for large scale gas turbine leaf
Piece causes depoling particularly difficult because type core length and cross sectional dimensions are larger.Improve alumina based ceramic core depoling rate
Method mainly has the core leach technics such as high temperature and pressure, pressure stirring and high-pressure jet, but the high requirements on the equipment.Another method is
The porosity of increase type core increases the contact area of depoling liquid and type core, to improve so that depoling liquid enters type core inner
Depoling rate.But since type core inner can have a certain amount of non-interconnected hole, the improved-type core depoling rate effect of this method has
Limit.
Therefore, the present invention provides a kind of turbine blade of gas turbine hot investment casting alumina based ceramic core manufacturing method
To solve the problems, such as this.
Summary of the invention
For above situation, for the defect for overcoming the prior art, it is accurate that the present invention provides a kind of turbine blade of gas turbine
Casting alumina based ceramic core manufacturing method, this method are suitable for solving large scale gas turbine blades casting process medium-sized
The disconnected core and core shift problem that core mechanical behavior under high temperature deficiency occurs, can also be effectively improved the depoling of blade cast form rear profile core
Performance is mainly based upon light-curing quick moulding method manufacture type core resin die, if there is dried resin silk inside resin die
Then alumina-based ceramic slurry is perfused by gel injection-moulding method in material in resin die, obtain ceramic core element with manufacture
Base；Intercommunicating pore structure is formed in type core inner after resin silk material burning mistake in resin die, facilitates the depoling of improved-type core
Energy；Meanwhile in type core sintering process, can in type core mullite synthesizing whisker, improve the mechanical behavior under high temperature of type core.
Turbine blade of gas turbine hot investment casting alumina based ceramic core manufacturing method, which is characterized in that including with
Lower step:
Step 1: production resin die；Using light-curing quick moulding method manufacture type core gel injection-moulding resin die,
Resin die includes resin silk material of resin die shell and its inside, resin silk material and resin die shell integrated molding；
Step 2: ceramic slurry is prepared；Monomer, crosslinking agent, dispersing agent are dissolved in deionized water, it is equal that mixing is then added
Ceramic slurry is made in even ceramic powders；
Step 3: ceramic core biscuit is prepared；Ceramic slurry described in step 2 is fed into resin in the step 1
In cavity between mold shell and resin silk material, the wet base of ceramic core is made after ceramic slurry in-situ solidifying, then chilled
Dry, the removing wet base internal moisture of ceramic core, is made ceramic core biscuit；
Step 4: pre-burning degreasing；Ceramic core biscuit in the step 3 is subjected to pre-burning degreasing, pre-burning degreasing is made
Ceramic core afterwards；
Step 5: high temperature sintering；Ceramic core after pre-burning degreasing in the step 4 is placed in corundum crucible, rigid
It is placed in 3%~6% aluminum fluoride powder inside beautiful crucible, covers crucible cover, then carries out high temperature sintering, it is former inside ceramic core
Position mullite synthesizing whisker；
Step 6: silica solution dipping is carried out to the ceramic core after synthesizing whisker, the silicon then dried in ceramic core is molten
Moisture in glue, and high temperature sintering is carried out to ceramic core again, obtain secondary mullite.
Preferably, the medium-sized core gel injection-moulding of the step 1 uses photosensitive resin through photocureable rapid shaping with resin die
Preparation.
Preferably, the resin silk material in the step 1 includes trunk resin silk material and branch's resin silk material, trunk resin
The cross section of silk material and branch's resin silk material can be rectangular or round；
For trunk resin silk material, when cross section is rectangular, side length is 1.0~1.5mm, and resin silk material section is circle
When, diameter of section is 1.0~1.5mm；
For branch's resin silk material, when cross section is rectangular, side length is 0.3~0.6mm, and resin silk material section is circle
When, diameter of section is 0.3~0.6mm.
Preferably, ceramic powders are made of basis material aluminium oxide and a small amount of mineralizer silica in the step 2,
Middle alumina ceramic powder uses partial size to be mixed for 40~60 μm, 5~10 μm and 1~3 μm of electro-corundum powder, accordingly
Account for solid phase powder quality respectively 30% and 50% and 17%, silicon oxide powder uses partial size for 1~3 μm of silica, accounts for
The 3% of solid phase powder quality.
Preferably, the monomer and crosslinking agent in the step 2, wherein monomer be acrylamide monomer, crosslinking agent N,
N '-methylene-bisacrylamide, monomer and crosslinking agent press (15~25): 1 mass ratio matches resulting mixture, monomer and crosslinking agent
The premixed liquid that mass concentration is 10%~20% is made in dissolution in deionized water；
Dispersing agent be 1%~3% sodium polyacrylate solution, additional amount be ceramic powders quality 2.0%~
3.0%；Ceramic powder accounts for the 50%~60% of slurry volume in ceramic slurry, and surplus is deionized water, monomer, crosslinking agent and divides
Powder；Initiator and catalyst are Ammonium Persulfate 98.5 aqueous solution and tetramethylethylenediamine aqueous solution, and the additional amount of the two is respectively pre-
The 0.5~1% and 0.1%~1% of mixed liquid quality.
Preferably, ceramic core needs to be placed in crucible in mullite crystal whisker synthesis process in the step 5, crucible
Need to cover crucible cover, and crucible bottom needs laying aluminum fluoride powder；Aluminum fluoride powder be aluminium oxide and siliconoxide mass it
The 3%~6% of sum.
Preferably, first slow rear fast heating method is taken in pre-burning degreasing in the step 4, and heating equipment is box resistance
Heating furnace, room temperature enter furnace and are warming up to 300 DEG C with 30 DEG C per hour, keep the temperature 0.5~1 hour；
Then 600 DEG C are warming up to 100 DEG C per hour~150 DEG C, keep the temperature 0.5~1 hour；
900 DEG C~1000 DEG C are warming up to 200 DEG C per hour~300 DEG C again, 3~5 hours is kept the temperature, cools to room with the furnace
Temperature.
Preferably, the step 5 high temperature sintering mullite synthesizing whisker is to be warming up to for 200 DEG C~300 DEG C per hour
1100 DEG C~1200 DEG C, 1~1.5 hour is kept the temperature, is then warming up to 1400 DEG C~1500 DEG C with 200 DEG C per hour~300 DEG C, is protected
Temperature 3~4 hours.
Preferably, in the step 6, after mullite synthesizing whisker, silica solution dipping, silicon are carried out to ceramic core green body
Colloidal sol mass fraction be 40%, impregnate silica solution after secondary high-temperature sintering with 200 DEG C per hour~300 DEG C be warming up to 1200 DEG C~
1300 DEG C, keep the temperature 2~3 hours.
Compared with prior art, the present invention has the following technical effect that:
The present invention prepares labyrinth ceramic core resin die by stereolithography, and simultaneously in a mold
If preparing dried resin silk material structure, ceramic slurry is then perfused in resin die by gel injection-moulding method and prepares ceramic mould
Core, since resin die and its internal silk material can be lost in subsequent skimming processes by burning, type core inner forms fine connection stream
Road structure, so that depoling liquid can be made to enter type core inner by runner during the core removal process, type core both ends and inside can be same
When contacted with depoling liquid, to increase the removing rate of core material.
The present invention, in type core inner mullite synthesizing whisker, can be effectively improved blade and be cast as by gas phase reaction method
The mechanical behavior under high temperature of the medium-sized core of shape process facilitates fracture and the core shift of reduction type core, improves vane manufacturing success rate；This
Outside, by then passing through XD method in type core inner synthesizing whisker, compared with type core inner interts continuous fiber, technique
Process is simpler, compared with adding staple fiber in ceramic slurry, can also reduce because of fiber increase slurry viscosity and to ceramics
The influence of slurry cavity filling energy.
Detailed description of the invention
Fig. 1 is the schematic diagram of ceramic core resin die.
Fig. 2 is the ceramic core schematic diagram being prepared.
Fig. 3 is the schematic cross-sectional view of ceramic core resin die.
Fig. 4 is the cross-sectional view schematic diagram of ceramic core.
Fig. 5 is the microstructure schematic diagram of ceramic core.
Wherein, 1: resin die fission A；2: resin die fission B；3: resin die fission C；4: ceramic core A；5: pottery
Porcelain type core B；6: ceramic core C；7: forming the resin silk material of ceramic core A inner flow passage structure；7a: trunk resin silk material；7b:
Branch's resin silk material；8: forming the resin silk material of ceramic core B inner flow passage structure；9: forming ceramic core C inner flow passage knot
The resin silk material of structure；10: ceramic core A inner flow passage structure；10a: sprue；10b: branch flow passage；11: in ceramic core B
Portion's flow passage structure；12: ceramic core C inner flow passage structure；13: type core matrix material oxidation aluminium；14: type core inner generates not
Carry out stone crystal whisker.
Specific embodiment
For the present invention aforementioned and other technology contents, feature and effect, in following cooperation with reference to figures 1 through Fig. 5 pairs
In the detailed description of embodiment, can clearly it present.The structure content being previously mentioned in following embodiment is attached with specification
Figure is reference.
In order to realize that above-mentioned task, the present invention take following technical solution:
Step 1: first use Introduction To Stereolithography manufacture type core resin die, mold include resin enclosure and
Internal resin silk material, resin silk material and resin die shell integrated molding；
Resin silk material is made of trunk resin silk material and branch's resin silk material, and wherein trunk resin silk material burns formation type after mistake
The sprue of core inner, branch's resin silk material burn the branch flow passage of formation type core inner after mistake, trunk resin silk material and branch tree
Rouge silk material cross section is rectangular or round；
For trunk resin silk material, when cross section is rectangular, side length is 1.0~1.5mm, when resin silk material cross section is
When round, diameter of section is 1.0~1.5mm；For branch's resin silk material, when cross section is rectangular, side length is 0.3~
0.6mm, when resin silk material section is round, diameter of section is 0.3~0.6mm.
The organic matter of monomer, crosslinking agent: being next dissolved in deionized water by step 2, then sequentially add dispersing agent and
Uniformly mixed aluminium oxide with and small amounts silicon ceramic powders, ceramic slurry is made after ball milling mixing is uniform, adds before perfusion
Enter initiator and catalyst, be uniformly mixed, in which:
Organic matter is acrylamide monomer, N, and N '-methylene-bisacrylamide crosslinking agent, the two is by (15~25): 1
Mass ratio matches resulting mixture, and the premixed liquid that mass concentration is 10%~20% is made in organic matter dissolution in deionized water；
Dispersing agent be 1%~3% sodium polyacrylate solution, additional amount be ceramic powders quality 2.0%~
3.0%；
Alumina ceramic powder is made of 40~60 μm, 5~10 μm and 1~3 μm electro-corundum powder mixing of partial size, three
The 30% and 50% and 17% of solid phase powder quality is accounted for respectively；
Silicon oxide powder partial size is 1~3 μm, accounts for the 3% of solid phase powder quality；
Ceramic powder accounts for the 50%~60% of slurry volume in ceramic slurry, surplus be deionized water, monomer, crosslinking agent and
Dispersing agent；
Initiator is Ammonium Persulfate 98.5 aqueous solution, and catalyst is tetramethylethylenediamine aqueous solution, and the additional amount of the two is respectively
The 0.5~1% of premixed liquid quality and 0.1%~1%.
Step 3: ceramic slurry is fed into resin die, between potting resin mould housing inner wall and resin silk material
Cavity area, the wet base of ceramic core that center includes resin silk material is made after ceramic slurry in-situ solidifying, then chilled dry
Dry removing green body internal moisture, obtains ceramic core biscuit.
Step 4: the type core after drying is put into box electric furnace, by pre-burning degreasing method burn lose resin die,
Organogel inside mould inside silk material and type core biscuit；
First slow rear fast heating method is taken in pre-burning degreasing, and room temperature enters furnace and is warming up to 300 DEG C with 30 DEG C per hour, heat preservation
0.5~1 hour；Then 600 DEG C are warming up to 100 DEG C per hour~150 DEG C, keep the temperature 0.5~1 hour；Finally with per hour 200
DEG C~300 DEG C be warming up to 900 DEG C~1000 DEG C, keep the temperature 3~5 hours, and cool to room temperature with the furnace.
Step 5: the type core after pre-burning degreasing is placed in corundum crucible, and crucible bottom is laid with aluminum fluoride powder, aluminum fluoride
Powder quality is the 3%~6% of ceramic powder quality, and crucible cover is then covered on crucible, is placed in box electric furnace again
Middle carry out high temperature sintering；
High temperature sintering generates whisker and is warming up to 1100 DEG C~1200 DEG C with 200 DEG C per hour~300 DEG C, and heat preservation 1-1.5 is small
When, 1400 DEG C~1500 DEG C then are warming up to 200 DEG C per hour~300 DEG C, keeps the temperature 3-4 hours；
Under high temperature environment, type core inner generates mullite crystal whisker, reaction equation such as formula (1) by gas phase reaction method
Shown in~(4):
6AlF3+3O2→6AlOF+12F (1)
Al2O3+2F→2AlOF+0.5O2 (2)
SiO2+8F→2SiF4+2O2 (3)
6AlOF+2SiF4+3.5O2→3Al2O3·2SiO2+14F (4)
Six in step: impregnation is carried out to type core using the silica solution of 40% mass fraction, then in drying-type core
Moisture in silica solution, and high temperature sintering is carried out to type core again；
High temperature sintering is warming up to 1200 DEG C~1300 DEG C with 200 DEG C per hour~300 DEG C again, keeps the temperature 2~3 hours；
Nano silicon oxide in silica solution generates secondary mullite with type core matrix material oxidation reactive aluminum at high temperature, increases
Big interface cohesion area and bond strength between mullite crystal whisker and type core matrix material oxidation aluminium, to improve whisker
To the humidification of type core；Meanwhile secondary mullite itself is also a kind of High-Temperature Strengthening phase, can be further improved type core high temperature
Mechanical property.
It will be detailed below the detailed construction and principle in each step:
The present invention is a kind of for turbine blade of gas turbine hot investment casting alumina based ceramic core manufacturing method, packet
Include following steps:
Step 1
Using light-curing quick moulding method manufacture type core resin die, resin die wall thickness is about 0.8~1.5mm.
The resin die contains resin die fission A1, resin die fission B2 and resin die fission C3, uses respectively
In gel casting three different ceramic core A4, ceramic core B5 and ceramic core C6.In resin die fission A1, tree
In rouge mold fission B2 and resin die fission C3, it is prepared for being used to form the resin of ceramic core A inner flow passage structure respectively
Silk material 7, the resin silk material 8 for forming ceramic core B inner flow passage structure and the resin silk for forming ceramic core C inner flow passage structure
Material 9.The resin silk material 7 of ceramic core A inner flow passage structure is wherein formed by trunk resin silk material 7a and branch resin silk material 7b
Composition；The resin silk material 8 of ceramic core B inner flow passage structure is formed by trunk resin silk material 7a and branch's resin silk material 7b group
At；The resin silk material 9 for forming ceramic core C inner flow passage structure is made of trunk resin silk material 7a and branch resin silk material 7b.
The trunk resin silk material cross sectional dimensions for forming main runner structure is 1mm × 1mm, forms branch's resin silk of branch flow passage structure
Material cross-sectional dimension is 0.4mm × 0.4mm, and branch's resin silk material both ends are apart from type core outer rim 2-3mm.
Step 2
Prepare gel injection-moulding ceramic core biscuit.
Organic matter is dissolved in deionized water first, premixed liquid is made, ceramic powders is then added, ceramic slurry is made, fill
Initiator and catalyst are added before note, is uniformly mixed, it is 50%~60% that wherein ceramic powder, which accounts for the volume ratio of slurry,；Organic matter
For acrylamide monomer, N, N '-methylene-bisacrylamide presses (15~25): the mixture that 1 mass ratio is made into, go from
Mass concentration is 10%~20% in sub- water；Initiator and catalyst are that Ammonium Persulfate 98.5 aqueous solution and tetramethylethylenediamine are water-soluble
Liquid, the additional amount of the two are respectively the 0.5~1% and 0.1%~1% of premixed liquid quality.
Ceramic slurry is fed into resin die, the chamber between potting resin mould housing inner wall and internal resin silk material
The wet base of ceramic core, then freeze-dried removal type core inner moisture are made after ceramic slurry in-situ solidifying, obtains for body region
Ceramic core biscuit.
Step 3
Pre-burning degreasing, removal type core inner resin silk material are carried out to ceramic core.
First slow rear fast heating method is taken in pre-burning degreasing, and heating equipment is box resistance-heated furnace, and room temperature enters furnace with every
30 DEG C of hour is warming up to 300 DEG C, keeps the temperature 0.5~1 hour；Then 600 DEG C are warming up to 100 DEG C per hour~150 DEG C, heat preservation
0.5~1 hour；900 DEG C~1000 DEG C are warming up to 200 DEG C per hour~300 DEG C again, keeps the temperature 3~5 hours；It cools to the furnace
Room temperature, obtains the ceramic core A inner flow passage structure 10 with inner flow passage structure, ceramic core A inner flow passage structure 10 by
Sprue 10a and branch flow passage 10b composition；Ceramic core B inner flow passage structure 11 is by sprue 10a and branch flow passage 10b group
At；Ceramic core C inner flow passage structure 12 is made of sprue 10a and branch flow passage 10b.
Runner can be maintained in type core after type core high temperature sintering, blade casting, thus in type core subtractive process
It can be improved the depoling efficiency of type core.
Step 4
Manufacture Whisker-reinforced ceramic type core.
In corundum crucible bottom laying aluminum fluoride, aluminum fluoride quality accounts for the 4% of ceramic core gross mass, then sets type core
Enter in crucible and cover crucible cover, then crucible is placed in box resistance-heated furnace and carries out high temperature sintering mullite synthesizing crystalline substance
Palpus.
The sintering process of synthesizing whisker is to be warming up to 1100 DEG C~1200 DEG C for 200 DEG C~300 DEG C per hour, heat preservation 1~1.5
Hour, 1400 DEG C~1500 DEG C then are warming up to 200 DEG C per hour~300 DEG C, keeps the temperature 3~4 hours.
React under aluminum fluoride high temperature with oxygen and generate gas, and with aluminium oxide and silica gas phase reaction, formation type in-core
The mullite crystal whisker 14 that portion generates, the mullite crystal whisker 14 that type core inner generates bridge composing type core matrix material oxidation aluminium 13,
The humidification to ceramic core is played in turn.
Step 5
Silica solution impregnation is carried out to type core, silica solution mass fraction is 40%.
Then type core is placed into baking oven, the moisture in silica solution in drying-type core, and type core is carried out again high
Temperature sintering.
High temperature sintering is warming up to 1200 DEG C~1300 DEG C with 200 DEG C per hour~300 DEG C, keeps the temperature 2~3 hours.Silica solution
In nano silicon oxide generate secondary mullite with oxidation reactive aluminum at high temperature, secondary mullite can increase to form type in-core
The interface cohesion area and bond strength between mullite crystal whisker 14 and type core matrix material oxidation aluminium 13 that portion generates, to mention
High humidification of the whisker to type core, while as a kind of High-Temperature Strengthening phase, secondary mullite can further enhance type core
Mechanical behavior under high temperature.3 high temperature anti-bending test experiments show prepared 1500 DEG C of elevated temperature strengths of type core sample up to 17
~18MPa.
In conclusion manufacturing center of the present invention has micro-flow path structure, the internal gas turbine containing mullite crystal whisker
Turbo blade alumina based ceramic core, sharpest edges are that the oxidation of large scale industry gas turbine turbo blade can be improved
The depoling performance of Al-base ceramic type core, at the same can effectively solve the medium-sized core mechanical behavior under high temperature of blade investment casting process it is insufficient,
The problem of being easy disconnected core core shift.In addition, the present invention, which manufactures inside using light-curing quick moulding method, contains fine resin silk
The type core resin die of material structure, resin silk material structure size is easy to adjust and form, therefore technical process is simple and easy to control.
Claims (9)
1. turbine blade of gas turbine hot investment casting alumina based ceramic core manufacturing method, which is characterized in that including following
Step:
Step 1: production resin die；Utilize light-curing quick moulding method manufacture type core gel injection-moulding resin die, resin
Mold includes resin silk material of resin die shell and its inside, resin silk material and resin die shell integrated molding；
Step 2: ceramic slurry is prepared；Monomer, crosslinking agent, dispersing agent are dissolved in deionized water, then addition is uniformly mixed
Ceramic slurry is made in ceramic powders；
Step 3: ceramic core biscuit is prepared；Ceramic slurry described in step 2 is fed into resin die in the step 1
In cavity between shell and resin silk material, the obtained wet base of ceramic core after ceramic slurry in-situ solidifying, then freeze-dried,
The wet base internal moisture of ceramic core is removed, ceramic core biscuit is made；
Step 4: pre-burning degreasing；Ceramic core biscuit in the step 3 is subjected to pre-burning degreasing, after pre-burning degreasing is made
Ceramic core；
Step 5: high temperature sintering；Ceramic core after pre-burning degreasing in the step 4 is placed in corundum crucible, in corundum earthenware
It is placed in 3%~6% aluminum fluoride powder inside crucible, covers crucible cover, then carries out high temperature sintering, is synthesized in ceramic core internal in-situ
Mullite crystal whisker；
Step 6: carrying out silica solution dipping to the ceramic core after synthesizing whisker, then dries in the silica solution in ceramic core
Moisture, and again to ceramic core carry out high temperature sintering, obtain secondary mullite.
2. turbine blade of gas turbine hot investment casting alumina based ceramic core manufacturing method according to claim 1,
It is characterized in that, the medium-sized core gel injection-moulding of step 1 uses photosensitive resin through photocureable rapid shaping system with resin die
It is standby.
3. turbine blade of gas turbine hot investment casting alumina based ceramic core manufacturing method according to claim 1,
It is characterized in that, the resin silk material in the step 1 includes trunk resin silk material and branch's resin silk material, trunk resin silk material
Cross section with branch resin silk material can be rectangular or round；
For trunk resin silk material, when cross section is rectangular, side length is 1.0~1.5mm, when resin silk material section is round,
Diameter of section is 1.0~1.5mm；
For branch's resin silk material, when cross section is rectangular, side length is 0.3~0.6mm, when resin silk material section is round,
Diameter of section is 0.3~0.6mm.
4. turbine blade of gas turbine hot investment casting alumina based ceramic core manufacturing method according to claim 1,
It is characterized in that, ceramic powders are made of basis material aluminium oxide and a small amount of mineralizer silica in the step 2, wherein oxygen
Changing aluminium ceramic powders uses partial size to be mixed for 40~60 μm, 5~10 μm and 1~3 μm of electro-corundum powder, and corresponding point
The 30% and 50% and 17% of solid phase powder quality is not accounted for, and silicon oxide powder uses partial size for 1~3 μm of silica, accounts for solid phase powder
The 3% of quality.
5. turbine blade of gas turbine hot investment casting alumina based ceramic core manufacturing method according to claim 1,
It is characterized in that, monomer and crosslinking agent in the step 2, wherein monomer is acrylamide monomer, crosslinking agent N, N '-
Methylene-bisacrylamide, monomer and crosslinking agent press (15~25): 1 mass ratio matches resulting mixture, monomer and crosslinking agent dissolution
The premixed liquid that mass concentration is 10%~20% is made in deionized water；
The sodium polyacrylate solution that dispersing agent is 1%~3%, additional amount is the 2.0%~3.0% of ceramic powders quality；Ceramic slurry
Ceramic powder accounts for the 50%~60% of slurry volume in material, and surplus is deionized water, monomer, crosslinking agent and dispersing agent；Initiator and
Catalyst is Ammonium Persulfate 98.5 aqueous solution and tetramethylethylenediamine aqueous solution, and the additional amount of the two is respectively the 0.5 of premixed liquid quality
~1% and 0.1%~1%.
6. turbine blade of gas turbine hot investment casting alumina based ceramic core manufacturing method according to claim 1,
It is characterized in that, ceramic core needs to be placed in crucible in mullite crystal whisker synthesis process in the step 5, crucible needs
Crucible cover is covered, and crucible bottom needs laying aluminum fluoride powder；Aluminum fluoride powder is the sum of aluminium oxide and siliconoxide mass
3%~6%.
7. turbine blade of gas turbine hot investment casting alumina based ceramic core manufacturing method according to claim 1,
It is characterized in that, first slow rear fast heating method is taken in pre-burning degreasing in the step 4, heating equipment is box resistance heating
Furnace, room temperature enter furnace and are warming up to 300 DEG C with 30 DEG C per hour, keep the temperature 0.5~1 hour；
Then 600 DEG C are warming up to 100 DEG C per hour~150 DEG C, keep the temperature 0.5~1 hour；
900 DEG C~1000 DEG C are warming up to 200 DEG C per hour~300 DEG C again, 3~5 hours is kept the temperature, cools to room temperature with the furnace.
8. turbine blade of gas turbine hot investment casting alumina based ceramic core manufacturing method according to claim 1,
It is characterized in that, the step 5 high temperature sintering mullite synthesizing whisker is to be warming up to 1100 DEG C for 200 DEG C~300 DEG C per hour
~1200 DEG C, 1~1.5 hour is kept the temperature, is then warming up to 1400 DEG C~1500 DEG C with 200 DEG C per hour~300 DEG C, heat preservation 3~4
Hour.
9. turbine blade of gas turbine hot investment casting alumina based ceramic core manufacturing method according to claim 1,
It is characterized in that, after mullite synthesizing whisker, carrying out silica solution dipping, silica solution to ceramic core green body in the step 6
Mass fraction is 40%, and secondary high-temperature sintering is warming up to 1200 DEG C~1300 with 200 DEG C per hour~300 DEG C after dipping silica solution
DEG C, keep the temperature 2~3 hours.
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