CN1317095C - Crystalloid laminae composited from single crystal and directional column crystal and preparing method - Google Patents
Crystalloid laminae composited from single crystal and directional column crystal and preparing method Download PDFInfo
- Publication number
- CN1317095C CN1317095C CNB2004100211935A CN200410021193A CN1317095C CN 1317095 C CN1317095 C CN 1317095C CN B2004100211935 A CNB2004100211935 A CN B2004100211935A CN 200410021193 A CN200410021193 A CN 200410021193A CN 1317095 C CN1317095 C CN 1317095C
- Authority
- CN
- China
- Prior art keywords
- blade
- crystal
- directional
- monocrystalline
- columnargrain
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Fee Related
Links
- 239000013078 crystal Substances 0.000 title claims abstract description 107
- 238000000034 method Methods 0.000 title claims abstract description 36
- 238000007711 solidification Methods 0.000 claims abstract description 32
- 230000008023 solidification Effects 0.000 claims abstract description 32
- 150000001875 compounds Chemical class 0.000 claims abstract description 31
- 239000000463 material Substances 0.000 claims abstract description 20
- 238000005266 casting Methods 0.000 claims abstract description 18
- 238000004519 manufacturing process Methods 0.000 claims abstract description 15
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 14
- 239000000956 alloy Substances 0.000 claims abstract description 14
- 239000007788 liquid Substances 0.000 claims abstract description 6
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 31
- 229910002804 graphite Inorganic materials 0.000 claims description 31
- 239000010439 graphite Substances 0.000 claims description 31
- 238000007713 directional crystallization Methods 0.000 claims description 10
- 230000015572 biosynthetic process Effects 0.000 claims description 4
- 238000005755 formation reaction Methods 0.000 claims description 4
- 238000002425 crystallisation Methods 0.000 abstract description 14
- 230000008025 crystallization Effects 0.000 abstract description 12
- 238000005495 investment casting Methods 0.000 abstract description 2
- 238000010438 heat treatment Methods 0.000 abstract 2
- 230000008018 melting Effects 0.000 abstract 1
- 238000002844 melting Methods 0.000 abstract 1
- 239000007789 gas Substances 0.000 description 14
- 238000011161 development Methods 0.000 description 9
- 238000005516 engineering process Methods 0.000 description 8
- 238000005070 sampling Methods 0.000 description 6
- 238000012360 testing method Methods 0.000 description 6
- 238000009661 fatigue test Methods 0.000 description 5
- 238000011160 research Methods 0.000 description 5
- 208000037656 Respiratory Sounds Diseases 0.000 description 3
- 238000013461 design Methods 0.000 description 3
- 238000009826 distribution Methods 0.000 description 3
- 238000011056 performance test Methods 0.000 description 3
- RZJQYRCNDBMIAG-UHFFFAOYSA-N [Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Zn].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn] Chemical class [Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Zn].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn] RZJQYRCNDBMIAG-UHFFFAOYSA-N 0.000 description 2
- 230000003197 catalytic effect Effects 0.000 description 2
- 239000002131 composite material Substances 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 230000005496 eutectics Effects 0.000 description 2
- 239000007791 liquid phase Substances 0.000 description 2
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 description 2
- 238000012827 research and development Methods 0.000 description 2
- 229910000601 superalloy Inorganic materials 0.000 description 2
- 230000031068 symbiosis, encompassing mutualism through parasitism Effects 0.000 description 2
- 239000008186 active pharmaceutical agent Substances 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000003245 coal Substances 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 210000001787 dendrite Anatomy 0.000 description 1
- 239000012530 fluid Substances 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 239000003345 natural gas Substances 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
Images
Landscapes
- Crystals, And After-Treatments Of Crystals (AREA)
Abstract
The present invention belongs to the fields of high temperature alloy precision casting, new material and a new process, particularly to a novel compound crystallization blade of single crystal and oriented column crystal and a making technique thereof. The present invention is used for developing and producing various types of high temperature alloy oriented solidification material and blades. The blade is composed of two crystal forms: the middle part of the blade has oriented column crystal, and an air input side and an air exhaust side of the blade have single crystal. The making method comprises the steps that a compound crystallizer is installed on a crystallizer of an oriented crystallization furnace; the degree of superheat of heating and melting is from 100 to 150 DEG C; the heating temperature of a casting mold heater is adjusted to the upper region temperature of 1500 to 1530 DEG C and the lower region temperature of 1550 to 1580 DEG C; when liquid alloy is poured into a casting mold, the casting mold starts to move downwards, and the downward moving speed of the casting mold is from 5 to 7 mm/min. The compound crystallization blade of the single crystal and the oriented column crystal has the advantages of higher combination property, simple making method and easy operation; the compound crystallization blade of the single crystal and the oriented column crystal can be applied to the production of gas turbine blades by high temperature alloy.
Description
Technical field
The invention belongs to the high temperature alloy precision casting category, new material and new technology field are specially novel monocrystalline and directional columnargrain compound crystal blade and manufacturing technology thereof, are used to develop and produce the material and the blade of various types of high temperature alloy directional solidifications.
Background technology
The energy is the power of the development of the national economy, the research and development of high performance gas-turbine engine are the required ideal power of sustainable development systems, developed country all pays close attention the research and development of gas turbine as the science and technology strategy of first developing, and obtains emphasis, development fast.In order to realize China's energy sustainable development strategy, the energy policy of country has also been done important adjustment, greatly develop the clean combustion of coal technology, development of fields, transfering natural gas from the west to the east or the like.Therefore, country also gas turbine as giving priority to direction, one of key technology of gas turbine development is its turbo blade material and manufacturing process thereof, for this reason the Chinese Academy of Sciences the research of industrial gas turbine engine bucket material and manufacturing process thereof as Tenth Five-Year Plan Period important research and development program element on the schedule, research institute develops at metal.
The successful experience and the technology of blade of aviation engine normally received in the development of gas turbine blades material and technology.Therefore, Xian Jin high temperature alloy directional solidification technique also is put into the directional crystalli zation blade of developing industry gas turbine.The crystallographic orientation of blade is meant that blade controls direction of heat flow in process of setting, makes the direction growth of crystallization along the parallel blade principal axes of stress, forms the columanar structure of oriented growth.Because directional crystalli zation blade has been eliminated horizontal crystal boundary, its performance and service life are significantly improved than the equiax crystal blade.If in the directional solidification process, further manage only to make a grain orientation growth, obtain single crystal blade at last, its performance can be further enhanced, because monocrystalline has not only been eliminated horizontal crystal boundary, and vertically crystal boundary has not existed yet.
Yet the blade that blade that aero-engine is used and industry gas turbine are used has dimensionally than big difference.The former length generally has only about 100mm, heavily about 250 grams; And gas turbine blades reaches more than the hundreds of millimeter, and weight is at least more than several kilograms.Because characteristics such as the gas turbine blades size is big, weight is big, heat is big have increased suitable difficulty therefore for the development of the directed crystallisation process of this big blade, if it is just more difficult to make it generate single crystal blade.
Summary of the invention
The object of the present invention is to provide the higher novel monocrystalline of a kind of combination property and directional columnargrain compound crystal blade and manufacture method thereof.
Technical scheme of the present invention is:
A kind of monocrystalline and directional columnargrain compound crystal blade, this blade is made up of two kinds of crystal formations: for directional columnargrain, is monocrystalline on the inlet and outlet limit of blade at the blade middle part.
Described monocrystalline width can be 20～30mm.
The manufacture method of above-mentioned monocrystalline and directional columnargrain compound crystal blade, concrete steps are as follows:
1) graphite mold is installed on the crystallizer of directional crystallization furnace, comprise graphite mold monocrystalline crystal selector, directional columnargrain crystal selector and directional solidification open the beginning section, the two ends of monocrystalline crystal selector, directional columnargrain crystal selector are all opened the beginning section with integral shroud, directional solidification and are communicated with, wherein monocrystalline crystal selector quantity is two, correspond respectively to the inlet and outlet limit of blade, the directional columnargrain crystal selector is corresponding to the blade middle part, and directional solidification opens the beginning section and is communicated with directional crystallization furnace;
2) process conditions:
The degree of superheat of heat fused is 100～150 ℃, and the heating-up temperature of casting mold heater is adjusted into 1500～1530 ℃ in district, 1550～1580 ℃ of inferior segments;
3) after liquid alloy poured into casting mold, casting mold began to move down, and under the condition of above-mentioned directional solidification, adopted the casting mold of 5-7mm/min to move down speed.
4, according to the manufacture method of described monocrystalline of claim 3 and directional columnargrain compound crystal blade, it is characterized in that: the material of described blade is a high temperature alloy.
Described monocrystalline crystal selector can be monocrystalline spiral crystal selector.
Described directional columnargrain crystal selector can be bulk or column, and wherein column crystal selector quantity is 3～5.
The invention has the beneficial effects as follows:
1, monocrystalline of the present invention and directional columnargrain compound crystal blade combination property are higher.This blade is made up of two kinds of crystal formations: for directional columnargrain, is monocrystalline with certain width on the inlet and outlet limit of blade at the blade middle part.Directional crystalli zation blade has been eliminated horizontal crystal boundary, its performance and service life are significantly improved than the equiax crystal blade, if in the directional solidification process, further manage only to make a grain orientation growth, obtain single crystal blade at last, its performance can be further enhanced, because monocrystalline has not only been eliminated horizontal crystal boundary, and vertically crystal boundary has not existed yet.The performance of the institutional framework decision material of material, the performance of material reflects the situation of its tissue, the performance of blade and its institutional framework reflect the good quality of this blade jointly.
2, simple, the easy row of the manufacture method of monocrystalline of the present invention and directional columnargrain compound crystal blade.This method adopts corresponding directional solidification processes condition to add " graphite mold " of particular design, graphite mold is installed on the crystallizer of directional crystallization furnace, graphite mold comprises the monocrystalline crystal selector, directional columnargrain crystal selector and directional solidification open the beginning section, the monocrystalline crystal selector, equal and the integral shroud in the two ends of directional columnargrain crystal selector, directional solidification opens the beginning section and is communicated with, wherein monocrystalline crystal selector quantity is two, correspond respectively to advancing of blade, the exhaust limit, the directional columnargrain crystal selector is corresponding to the blade middle part, directional solidification opens the beginning section and is communicated with directional crystallization furnace, and " graphite mold " played the catalytic action of monocrystalline and directional columnargrain blade.
3, the present invention goes for high temperature alloy and produces gas turbine blades.
Description of drawings
Fig. 1 is the shape of aero-engine and industrial gas turbine engine bucket, the contrast photo in kind of size.
Fig. 2 is the big blade of crystallographic orientation of the present invention photo in kind.
Fig. 3 organizes photo for the monocrystalline and the cylindrulite compound crystal of blade of the present invention.
Fig. 4 is the sampling point schematic diagram of Blade Properties test of the present invention.
Fig. 5 a～d is respectively 6,5,4, No. 2 sampling point arborescent structure distribution pictures among Fig. 4.
Fig. 6 a～d is respectively 6,5,4, No. 2 sampling point eutectic structure distribution pictures among Fig. 4.
Fig. 7 a～d is respectively 6,5,4, No. 2 sampling point carbide Tissue distribution pictures among Fig. 4.
Fig. 8 is the monocrystalline and the directional columnargrain compound crystal blade picture of band graphite mold of the present invention.
Fig. 9 for graphite mold structure of the present invention and with blade annexation schematic diagram.
Figure 10 is the A-A cutaway view of Fig. 9.
Figure 11 is the B-B cutaway view of Fig. 9.
Figure 12 is the monocrystalline and the directional columnargrain compound crystal blade photo of the another kind of graphite mold of the present invention.
The specific embodiment
Present embodiment selects for use the big blade (300mm, weigh 2500 gram) of 5000 serial gas turbines to be research object, the work that conducts a research, and the material of this blade adopts directionally solidified superalloy, DS superalloy GTD-111.Fig. 1 illustrates the shape of aero-engine and selected industrial gas turbine engine bucket, the contrast photo in kind of size.
The present invention is in the development process of gas turbine blades directed crystallisation process, has both finished the research of big blades oriented crystallization processes, develops the big blade of crystallographic orientation, as shown in Figure 2.Succeeded in developing simultaneously the new blade of a kind of monocrystalline and directed compound crystal again.This blade is made up of two kinds of crystal formations: be directional columnargrain at the blade middle part, (present embodiment is 20～30mm) monocrystalline in order to have certain width on the inlet and outlet limit of blade.Fig. 3 shows the crystalline structure of this new blade.By photo as can be seen, this is symbiosis, the common NEW TYPE OF COMPOSITE crystallization blade of growing and coexisting that a kind of monocrystalline and directional columnargrain form in process of setting.
1, monocrystalline and directional columnargrain compound crystal Blade Properties.In order to understand the performance of monocrystalline and directional columnargrain compound crystal blade, special different parts from this blade cuts different samples and carries out performance test.Fig. 4 illustrates the sampling point of this blade.
(1) cold and hot fatigue.Cut cold and hot fatigue testing specimen respectively from directional columnargrain district, blade leading edge single-crystal region and blade middle part and test comparison.Cold and hot fatigue test is to utilize the cold and hot rapid variation of temperature to cause the material production crackle, with the cold and hot fatigue strength of experimental material.This test is similar at the changing condition of the suffered rapid heat cycle of use to blade.Therefore, selecting cold and hot fatigue test purpose for use also is to be to simulate the blade behaviour in service, and material is compared.It is as shown in the table for result of the test.The monocrystalline sample does not find that through 66 cold and hot fatigue tests crackle produces, and does not still have the sign that cracks.The directional columnargrain sample at sample edge generation crackle, and passes loose and oxidized zone extension expansion along crystal boundary through 19 cold and hot fatigue tests.Contrast the superiority of visible mono-crystalline structures thus.
(2) high-temperature and durable and instantaneous performance.The high-temperature and durable and the high temperature snap sample that cut Φ 3mm from directional columnargrain district, blade middle part are tested.Test result is as shown in table 1.From test result as can be seen, no matter be on blade top, still in the blade bottom, the sampling performance meets or exceeds the requirement of material defined.Carry out metallographic examination again for the sample of doing performance test, in the size of dendrite, eutectic and the carbide of blade upper and lower part with distribute all relatively good.Shown in Fig. 5,6,7, the performance of the institutional framework of material decision material, the performance of material reflects the situation of its tissue.The performance of blade and its institutional framework reflect the good quality of this blade jointly.
(3) tabular properties of sample.The inlet and outlet limit of blade all is relatively thinner, in order to understand performance in exhaust limit single-crystal region, the tabular sample that cuts thick 2mm from blade exhaust limit single-crystal region carries out the instantaneous performance test of high temperature, the result is as shown in table 1, measured data is higher than required value far away, and this also reflects the superiority of mono-crystalline structures.
Table 1 monocrystalline and directional columnargrain compound crystal Blade Properties
| Numbering | Crystalline state | Performance requirement | Measured | Remarks | |
| 1 | Monocrystalline | Cold and hot fatigue | 66 flawlesses of 1100 ℃ of shrends | Sample keeps blade leading | |
| 2 | Cylindrulite | Cold and hot fatigue | 19 intergranular cracks of 1100 ℃ of shrends | Sample is made blade leading | |
| 3 | Monocrystalline | 980℃ σb≥400MPa δ％≥10％ | 980℃ σb＝492MPa δ％＝28％ | Tabular thickness of sample 2mm | |
| 4 | Cylindrulite | 816℃ 483MPa≥60h | 816℃ 483MPa≥200h | The little coupon of Φ 3mm | |
| 5 | Cylindrulite | 980℃ σb≥400MPa δ％≥10％ | 980℃ σb＝521MPa δ％＝19％ | The little coupon of Φ 3mm | |
| 6 | Cylindrulite | 980℃ 190MPa≥50h | 980℃ 190MPa≥62h | The little coupon of Φ 3mm | |
| 7 | Cylindrulite | Room temperature σ b 〉=900MPa δ % 〉=5% | Room temperature σ b 〉=1189MPa δ % 〉=6.7% | The little coupon of Φ 3mm | |
| 8 | Cylindrulite (laterally) | - | 980℃ 190MPa＝48.9h | The little coupon of Φ 3mm |
2, the manufacture method of monocrystalline and directional columnargrain compound crystal blade.According to monocrystalline and directional columnargrain crystallization principle, except its directional solidification processes parameter being carried out necessary adjustment, mainly be for this reason particular design one " graphite mold ".Should " graphite mold " form, promptly open the beginning section and form by monocrystalline spiral crystal selector, directional columnargrain crystal selector and directional solidification by three parts.During use " graphite mold " integral shroud with blade is joined, two monocrystalline crystal selectors on " graphite mold " are aimed at the inlet and outlet limit of blade respectively, and the directional columnargrain crystal selector of " graphite mold " is aimed at the blade middle part.Fig. 8 shows the monocrystalline and the directional columnargrain compound crystal blade of the band of succeeding in developing " graphite mold ".
Succeeding in developing of novel monocrystalline and directional columnargrain compound crystal blade is the result of ingenious utilization monocrystalline and crystallographic orientation rule.Blade is in the directional solidification process, and crystallization grows up to the crystalline solid of which kind of type, depends on that mainly solidifying regional liquid phase alloy temperature gradient distributes.Big blade is when directional solidification, because its inlet and outlet limit is thinner relatively, amount of liquid is few, solidifies factors such as very fast, that the solid phase thermal conductivity factor is big, causes the thermograde of its solidification zone liquid phase alloy to be higher than the blade middle part of growing with the cross section directional columnargrain.So, just formed at blade inlet and outlet limit growing single-crystal with in the condition of the growing oriented cylindrulite in blade middle part.That is to say to have possessed monocrystalline and directional columnargrain symbiosis in the blade same cross-sectional, be total to long condition.As long as provide nucleus just can make it grow two kinds of crystallizations simultaneously.Monocrystalline and directional columnargrain " graphite mold " just can play this effect.Like this, under the process conditions of directional solidification, just can make it to crystallize into this new blade.
1, " graphite mold " structure and it and being connected of blade 1." graphite mold " is by monocrystalline spiral crystal selector 3 and directional columnargrain crystal selector 4 be combined intos.It comprises three parts: monocrystalline crystal selector 3, directional columnargrain crystal selector 4 and directional solidification open beginning section 5.Fig. 9 illustrates its structure and its situation that is connected with blade.
Figure 10 is the monocrystalline spiral crystal selector 3 of " graphite mold " and integral shroud 2 link positions of directional columnargrain crystal selector 4 and blade 1.Figure 11 opens the combined situation of beginning section 5 for monocrystalline crystal selector 3, directional columnargrain crystal selector 4 and directional solidification on " graphite mold ".
2, the effect of " graphite mold "
" graphite mold " of monocrystalline and directional columnargrain compound crystal blade is directly installed on the crystallizer of directional crystallization furnace.At the initial stage of directional solidification, after liquid alloy poured into casting mold, casting mold began to move down.Liquid alloy generates the tiny equiax crystal of one deck in the beginning section of opening of " graphite mold " under the Quench of crystallizer.In continuing process of setting, crystallization is under hot-fluid control, and tiny equiax crystal grows up to tiny directional columnargrain very soon, enters the crystal selector of monocrystalline crystal selector and directional columnargrain then respectively.In the monocrystalline crystal selector, unnecessary cylindrulite is limited, and has only a crystal grain to enter blade at last, for the inlet and outlet limit of blade provides the nucleus that can grow up to monocrystalline.In the crystal selector of directional columnargrain, the cylindrulite group of directional solidification rectifies direction with further permutation and combination, and the thin straight cylindrulite in (001) crystal orientation of preferred growth enters blade at first, for the cylindrulite that provides more straight that solidifies of blade middle part directional columnargrain is examined.Like this, under corresponding directional solidification processes, " graphite mold " just played the catalytic action of monocrystalline and directional columnargrain blade.
The enforcement of monocrystalline and directional columnargrain composite blading is exactly " graphite mold " that corresponding directional solidification processes condition adds particular design.
1, process conditions.The enforcement of monocrystalline and directional columnargrain compound crystal blade must possess minimum directional solidification processes condition.In order to help crystal growth, further adjust the heating-up temperature that improves pouring temperature and casting mold heater on this basis.For this reason, pouring temperature is brought up to 1550 ℃ by 1520 ℃.The heating-up temperature of casting mold heater is adjusted into 1500 ℃ in district, 1550 ℃ of inferior segments.
2, " graphite mold " and blade is connected.It must join with the integral shroud end of blade.That is to say, make monocrystalline and directional columnargrain compound crystal blade begin crystallization from the integral shroud end.
3, casting mold translational speed.Under the condition of above-mentioned directional solidification, the casting mold of employing 5-7mm/min moves down speed and all can obtain this new blade.
Under above-mentioned directional solidification condition, with another " graphite mold ", only the directional columnargrain crystal selector on above-mentioned " graphite mold " is changed into three columns by bulk, can obtain such blade equally, as shown in figure 12, explanation thus, the monocrystalline crystal selector on " graphite mold " are the keys of implementing.
Claims (6)
1, a kind of monocrystalline and directional columnargrain compound crystal blade is characterized in that this blade is made up of two kinds of crystal formations: being directional columnargrain at the blade middle part, is monocrystalline on the inlet and outlet limit of blade.
2, according to described monocrystalline of claim 1 and directional columnargrain compound crystal blade, it is characterized in that: described monocrystalline width is 20～30mm.
3, according to the manufacture method of described monocrystalline of claim 1 and directional columnargrain compound crystal blade, it is characterized in that concrete steps are as follows:
1) graphite mold is installed on the crystallizer of directional crystallization furnace, comprise graphite mold monocrystalline crystal selector, directional columnargrain crystal selector and directional solidification open the beginning section, the two ends of monocrystalline crystal selector, directional columnargrain crystal selector are all opened the beginning section with integral shroud, directional solidification and are communicated with, wherein monocrystalline crystal selector quantity is two, correspond respectively to the inlet and outlet limit of blade, the directional columnargrain crystal selector is corresponding to the blade middle part, and directional solidification opens the beginning section and is communicated with directional crystallization furnace;
2) process conditions:
The degree of superheat of heat fused is 100～150 ℃, and the heating-up temperature of casting mold heater is adjusted into 1500～1530 ℃ in district, 1550～1580 ℃ of inferior segments;
3) after liquid alloy poured into casting mold, casting mold began to move down, and under the condition of above-mentioned directional solidification, adopted the casting mold of 5-7mm/min to move down speed.
4, according to the manufacture method of described monocrystalline of claim 3 and directional columnargrain compound crystal blade, it is characterized in that: the material of described blade is a high temperature alloy.
5, according to the manufacture method of described monocrystalline of claim 3 and directional columnargrain compound crystal blade, it is characterized in that: described monocrystalline crystal selector is a monocrystalline spiral crystal selector.
6, according to the manufacture method of described monocrystalline of claim 3 and directional columnargrain compound crystal blade, it is characterized in that: described directional columnargrain crystal selector is bulk or column, and wherein column crystal selector quantity is 3～5.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2004100211935A CN1317095C (en) | 2004-02-25 | 2004-02-25 | Crystalloid laminae composited from single crystal and directional column crystal and preparing method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2004100211935A CN1317095C (en) | 2004-02-25 | 2004-02-25 | Crystalloid laminae composited from single crystal and directional column crystal and preparing method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1660524A CN1660524A (en) | 2005-08-31 |
| CN1317095C true CN1317095C (en) | 2007-05-23 |
Family
ID=35010247
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB2004100211935A Expired - Fee Related CN1317095C (en) | 2004-02-25 | 2004-02-25 | Crystalloid laminae composited from single crystal and directional column crystal and preparing method |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN1317095C (en) |
Families Citing this family (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20100071812A1 (en) * | 2008-09-25 | 2010-03-25 | General Electric Company | Unidirectionally-solidification process and castings formed thereby |
| CN102847917A (en) * | 2012-07-09 | 2013-01-02 | 沈阳黎明航空发动机(集团)有限责任公司 | Method for variable speed crystal pulling of ultrathin narrow-chord long allowance-free directional working blade |
| CN103736980B (en) * | 2013-12-30 | 2015-10-28 | 西安交通大学 | A kind of method determining casting mold angles in directional solidification casting |
| CN103736979B (en) * | 2013-12-30 | 2015-08-26 | 西安交通大学 | A kind of method determining casting mold putting position in directional solidification casting |
| US20150275677A1 (en) * | 2014-03-27 | 2015-10-01 | General Electric Company | Article for use in high stress environments having multiple grain structures |
| CN104289674B (en) * | 2014-10-24 | 2016-09-14 | 东方电气集团东方汽轮机有限公司 | Gas turbine cylindrulite guide vane casting method |
| CN104325083B (en) * | 2014-11-24 | 2016-06-29 | 沈阳黎明航空发动机(集团)有限责任公司 | A kind of block cast covering plate structure orientation turbo blade pouring technology method |
| CN104858399B (en) * | 2015-04-17 | 2016-04-20 | 北京航空航天大学 | A kind of functionally gradient single crystal blade material be combined into by two kinds of alloys and preparation method thereof with realize equipment |
| CN115026243B (en) * | 2022-06-10 | 2024-04-19 | 深圳市万泽航空科技有限责任公司 | Control method for outcrop crystals of directional blades |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN85106439A (en) * | 1985-08-27 | 1987-03-11 | 西屋电气公司 | Manufacture method with combustion turbine blade of monocrystal part |
| CN1089196A (en) * | 1992-03-21 | 1994-07-13 | 中国科学院长春光学精密机械研究所 | Integral precision casting process method for high-speed fan impeller |
| CN1123874A (en) * | 1993-08-06 | 1996-06-05 | 株式会社日立制作所 | Blade for gas turbine, manufacturing method of the same, and gas turbine including the blade |
| JPH08238561A (en) * | 1995-03-02 | 1996-09-17 | Mitsubishi Steel Mfg Co Ltd | Production of single crystal casting and producing device therefor |
| FR2734187A1 (en) * | 1981-09-25 | 1996-11-22 | Snecma | Casting and directional solidification. of a cluster of turbine rotor vanes |
| CN1278199A (en) * | 1997-10-27 | 2000-12-27 | 西门子西屋动力公司 | Turbine blades made from multiple signle crystasl cast superalloy segments |
| JP2002283043A (en) * | 2001-03-28 | 2002-10-02 | Mitsubishi Materials Corp | Method for producing turbine blade having unidirectional solidified columnar crystal structure and turbine blade produced by the method |
-
2004
- 2004-02-25 CN CNB2004100211935A patent/CN1317095C/en not_active Expired - Fee Related
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2734187A1 (en) * | 1981-09-25 | 1996-11-22 | Snecma | Casting and directional solidification. of a cluster of turbine rotor vanes |
| CN85106439A (en) * | 1985-08-27 | 1987-03-11 | 西屋电气公司 | Manufacture method with combustion turbine blade of monocrystal part |
| CN1089196A (en) * | 1992-03-21 | 1994-07-13 | 中国科学院长春光学精密机械研究所 | Integral precision casting process method for high-speed fan impeller |
| CN1123874A (en) * | 1993-08-06 | 1996-06-05 | 株式会社日立制作所 | Blade for gas turbine, manufacturing method of the same, and gas turbine including the blade |
| JPH08238561A (en) * | 1995-03-02 | 1996-09-17 | Mitsubishi Steel Mfg Co Ltd | Production of single crystal casting and producing device therefor |
| CN1278199A (en) * | 1997-10-27 | 2000-12-27 | 西门子西屋动力公司 | Turbine blades made from multiple signle crystasl cast superalloy segments |
| JP2002283043A (en) * | 2001-03-28 | 2002-10-02 | Mitsubishi Materials Corp | Method for producing turbine blade having unidirectional solidified columnar crystal structure and turbine blade produced by the method |
Also Published As
| Publication number | Publication date |
|---|---|
| CN1660524A (en) | 2005-08-31 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN1317095C (en) | Crystalloid laminae composited from single crystal and directional column crystal and preparing method | |
| CN103789598B (en) | A kind of directed TiAl-base alloy and preparation method thereof | |
| CN108913952B (en) | High-temperature alloy and preparation method thereof | |
| CN102108555B (en) | High-temperature perfect oxidation resistance type nickel-based single-crystal alloy and preparation method thereof | |
| CN104858399B (en) | A kind of functionally gradient single crystal blade material be combined into by two kinds of alloys and preparation method thereof with realize equipment | |
| CN102433466A (en) | Nickel and cobalt-based high-temperature alloy containing rare earth elements and preparation method thereof | |
| CN102011195A (en) | Preparation method of directional solidification high-Nb TiAl alloy single crystal | |
| CN102653832A (en) | Novel directed nickel-base high temperature alloy | |
| CN106636759A (en) | Platinum group element reinforced high-thermal stability and high-strength nickel-based single-crystal high-temperature alloy | |
| CN107034388A (en) | The preparation technology of nickel-base high-temperature single crystal alloy turbo blade | |
| CN107119325A (en) | A kind of method for eliminating laser 3D printing single crystal super alloy recrystallization tendency | |
| CN109773137A (en) | A method of preventing the formation of single crystal super alloy guide vane stray crystal defect | |
| CN2721283Y (en) | Composite crystallizer for single crystal and directional cylindrulite composite crystalline blade | |
| CN116900247B (en) | Preparation method of ceramic matrix composite and monocrystalline superalloy composite component | |
| CN105296809B (en) | A kind of high intensity precipitation strength cobalt-based single crystal super alloy and preparation method thereof | |
| CN110153373B (en) | High-flux preparation method of metal material solidification structure | |
| CN111168004A (en) | Method for forming single crystal part by gel casting integrated casting based on spiral crystal selector with seed crystal block embedded structure | |
| CN101255607A (en) | Method for preparing Ni3Al-based single-crystal refractory alloy by employing combination of seed crystal method and screw selecting method | |
| RU2532621C1 (en) | Device for casting of turbine blade with monocrystalline structure | |
| CN115044804A (en) | Nickel-based directional columnar crystal superalloy and preparation method and application thereof | |
| Singer | New materials for industrial gas turbines | |
| CN1280039C (en) | Silicon carbide shell production and use in directional solidification | |
| CN2629875Y (en) | silicon carbide section mould for directional solidification | |
| CN101525706B (en) | Modification method for enhancing high-temperature creep resistance in nickel-base single crystal superalloy | |
| JPH07247802A (en) | Manufacture of single crystal blade for gas turbine |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| C17 | Cessation of patent right | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20070523 Termination date: 20100225 |