CN103668461A - Method for preparing nickel-based superalloy Rene80 directionally-grown column crystal/single crystal alloy and manufacturing parts - Google Patents
Method for preparing nickel-based superalloy Rene80 directionally-grown column crystal/single crystal alloy and manufacturing parts Download PDFInfo
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Abstract
The invention relates to a method for preparing a nickel-based superalloy Rene80 directionally-grown column crystal/single crystal alloy and manufacturing parts, and belongs to the processing field of the laser materials. The method is carried out in atmosphere; a high-energy beam is taken as the heat source; the movement of the high-energy beam is achieved under the control of a numerical control system; the Rene80 powder flow conveyed by a carrier gas is smelted and deposited on a directionally-solidified nickel-based alloy substrate layer by layer; in this way, the nickel-based superalloy and parts having directionally-grown straight column crystal structure/single crystals and different cross-section shapes can be directly manufactured. The nickel-based alloy Rene80 directionally-grown column crystal/single crystal alloy parts manufactured by the method can be applied to manufacturing the hot end parts of naval ships, gas turbines and aero-engines.
Description
Technical field
The present invention relates to a kind of oriented growth cylindrulite and single crystal alloy preparation and component manufacture method, specifically refer to a kind of powder layer by layer deposition of continuous conveying, manufacture method that manufacture arbitrary shape has oriented growth cylindrulite and component of adopting.
Background technology
Directional freeze is that while utilizing alloy graining, crystal grain, along the principle of hot-fluid reverse direction growth, is controlled direction of heat flow, makes foundry goods along the foundry engieering of prescribed direction crystallization.Common foundry goods generally forms by the polycrystal without certain crystallization direction.The most outstanding achievement of directional solidification technique is the application in aircraft industry.Adopt directional solidification technique to produce to there is good thermal shock resistance, longer fatigue lifetime, the thin-walled hollow turbine blade of creep resistance and middle temperature plasticity preferably.
Directional freeze/single crystal alloy is owing to having reduced the transverse grain boundaries vertical with principal axes of stress direction, high temperature creep and the enduring quality of material have been significantly improved, can extend the work-ing life of the key parts such as aircraft engine, gas-turbine blade and naval vessel blade, because of but the preferred material of the high-temperature components such as aircraft engine.Monocrystalline Parts manufacturing technology has become one of more than 10 high-performance enginer key manufacture of thrust-weight ratio.The directional freeze Rene80 alloy material of take is example, its tensile property and creep life and the score of conventional cast Rene80 alloy phase you can well imagine 10-15% high and 1-3 doubly.And single crystal alloy is compared with qualitative solidified superalloy, price is higher, and performance does not significantly improve, and has just eliminated transverse grain boundaries.
Traditional directional freeze/single crystal alloy part adopts the method manufacture of casting.Take single crystal blade as example, and whole foundry goods is comprised of a crystal grain.Be after directionally solidified superalloy, further improve an approach of alloy strength and use temperature.The ideal tissue of single crystal blade foundry goods is blade root, blade and integral shroud, all the flawless heterogeneous single crystal of milli, consists of.Crystalline orientation should be < 100 > directions, and and blade principal axes of stress direction between do not depart from and should be greater than 10 degree.Single crystal casting can be used the equipment and process preparation identical with directional freeze, is only to add on the top of water-cooled chassis crystal selector or young brilliant with the difference of directional solidification castings, to control single crystal, enters foundry goods.
Phase late 1990s, the human hairs such as the Gaeumann of engineering college of Swiss Confederation understand laser metal extension forming technique (E-LMF), the monocrystal nickel-base alloy CMSX-4 of take in this technology is substrate, take CO2 laser as thermal source, to laser and substrate interaction area, send into continuously and melt the CMSX-4 powder that chemical constitution is single crystal alloy composition, realized the preparation of CMSX-4 single crystal alloy, and successfully for the reparation of single crystal blade.
But directional solidification blade or the subject matter of single crystal blade Foundry Production is exactly that manufacturing time is long no matter, yield rate is low.The laser of take is directly prepared monocrystalline and manufactures monocrystalline component also beyond example in the world as thermal source adopts directional freeze substrate and unidirectional solidification material.
Summary of the invention
The object of the invention is, provide a kind of and take high energy and count stream and be that thermal source adopts powder layer by layer deposition, the preparation of carrying continuously have oriented growth cylindrulite and single crystal alloy and manufacture the manufacture method that arbitrary shape has oriented growth cylindrulite and monocrystalline component.By the heat effect of high energy beam current, flow of powder melt deposition successively on the nickel-base alloy substrate of directional freeze, preparation has oriented growth cylindrulite and single crystal alloy and directly manufactures the nickel based super alloy Rene80 part with the straight and upright columnar structure/monocrystalline of oriented growth, different cross section shape.Its displacement angle of single crystal alloy of preparation is less than 10 °.The nickel-base alloy Rene80 oriented growth cylindrulite of this method manufacture and single crystal alloy component can be used for the manufacture of naval vessel, internal combustion turbine and aircraft engine hot junction part.
Rene80 oriented growth cylindrulite of the present invention and single crystal alloy component are achieved in that described method carries out in atmosphere, using high energy beam current as thermal source, the digital control system that moves through of high energy beam current has been controlled, the Rene80 flow of powder that carrier gas is carried melt deposition successively on the nickel-base alloy substrate of directional freeze, directly preparation has the alloy of the straight and upright columnar structure/monocrystalline of oriented growth, or directly manufactures the nickel based super alloy Rene80 part with the straight and upright columnar structure/monocrystalline of oriented growth, different cross section shape.
Described Rene80 oriented growth cylindrulite and single crystal alloy preparation and component manufacture method, is characterized in that: described equipment comprises:
A. a high energy beam current adopts laser beam, electron beam or beam-plasma as thermal source;
B. a directionally solidified superalloy substrate;
C. the powder conveying system of a set of conveying Rene80 powder: comprise powder feeder and powder-feeding nozzle; Wherein the function of powder-feeding nozzle comprises water-cooling system, plenum system, powder feed system etc.;
Alloy preparation or part manufacture process all complete in atmosphere, and in part manufacture process, the protection in liquid molten bath only carries shielding gas to realize by powder-feeding nozzle to Reciprocity of Laser & Materials district conveying powder time;
Concrete grammar comprises the following steps,
The first step: granularity is put into powder feeder for-200 orders～+ 325 object Rene80 powder;
Second step: adopt gripping unit that the nickel-base alloy base plate of directional freeze is clamped, be placed on worktable;
The 3rd step: argon gas is passed in powder feeder in the carrier gas of carrying as powder and powder-feeding nozzle and exported as shielding gas;
The 4th step: first open supply gas, powder conveyer, then start high energy beam current.At this moment powder be continuously fed into the interaction area of laser and substrate and enter laser and molten bath that substrate interact to form in; High energy beam current light source is along the cad model section track scanning that will build part, by the Rene80 powder of synchronous transport, successively melt deposition is on the nickel-base alloy plate of directional freeze, and preparation has the Rene80 part of different shapes and the size of oriented growth columanar structure; In oriented growth cylindrulite and single crystal alloy preparation process, laser power, powder sending quantity, laser speed of feed have determined width and height, laser scanning strategy and the z axial translation amount of the heat input in laser processing procedure, single track cladding line.The scope of above-mentioned parameter is respectively: laser power: 400-1200W, powder sending quantity: 8-12g/ divides, laser speed of feed: 200-600mm/ divides, z axial translation amount: 100-500um/ time.Rene80 oriented growth cylindrulite and single crystal alloy preparation and component manufacturing system figure are as shown in Figure 1.Here z axial translation amount is particularly important, it need to melt turn to dendrite or the equiax crystal that in laser processing procedure, occur fall completely, the base plate of current like this weld pool solidifies has the feature of oriented growth, and in laser solid forming process, the distribution schematic diagram of the interior different zones of drip molding as shown in Figure 2.
The advantage of Rene80 oriented growth cylindrulite of the present invention and single crystal alloy preparation and component manufacture is:
Invent and can, for the preparation of Rene80 oriented growth cylindrulite and single crystal alloy, also can directly manufacture the nickel based super alloy Rene80 part with the straight and upright columnar structure/monocrystalline of oriented growth, different cross section shape.
Preparation process does not need mould, use the high energy beam current of high-energy-density by Rene80 powder rapid melting, rapid solidification, can in liquid-solid interface forward position, set up and maintain the high thermograde along the direction of growth, realize the oriented growth of nickel-base alloy, thereby can prepare, there is the alloy of straight and upright columnar structure/monocrystalline and the nickel based super alloy Rene80 part of different cross section shape.
This preparation method carries out in atmosphere, but by the structure design of powder-feeding nozzle, realizes the protection of alloy material liquid towards molten bath and preparation.Oxidation, the nitrogenize in liquid molten bath have effectively been prevented.
This preparation method can also significantly shorten titanium alloy component manufacturing cycle, reduction manufacturing cost, improve the utilization ratio of material.
Inventive principle
In laser cladding forming process, mother metal, as cold junction, causes molten bath liquid-solid interface place thermograde and setting rate all larger, thereby in liquid molten bath, the growth of dendrite is epitaxy.The principal element that affects dendritic growth direction in liquid molten bath has the crystalline orientation of the preferred orientation of material, direction of heat flow and base plate.In liquid molten bath, the growth of dendrite is always perpendicular to liquid-solid interface, and the opposite direction of hot-fluid.When the preferred orientation of base plate is identical with the direction of hot-fluid, in liquid molten bath, the growth of dendrite will be along there being the direction of orientation to carry out.When the preferred orientation of base plate is different with the direction of hot-fluid, in liquid molten bath, the growth of dendrite will be along carrying out with the direction of heat flow direction that has a certain degree.
The drip molding microstructure obtaining in oriented growth cylindrulite and single crystal alloy preparation process is except from the epitaxially grown oriented freezing organization of substrate, drip molding top is because thermograde is low, setting rate is very fast, column crystal easily occur to the transformation of equiax crystal or at top, occur the dendrite that turns to of parallel sweep direction, these the two kinds dendrite that are different from the directed dendritic growth direction of extension all can be described as and turn to dendrite district.Turn to the formation of dendrite jointly determined by direction of heat flow and crystal preferred orientation.Crystal initial growth direction is between optimum crystalline orientation and maximum temperature gradient direction (being direction of heat flow), and along with thermograde G
lratio G with speed of growth R
lthe reducing of/R tends to optimum crystallographic direction growth gradually, and direction of heat flow in molten bath is affected by melting pool shape mainly.The formation of equiax crystal is that main thermograde and setting rate in process of setting determines.When carrying out multilayer cladding and pile up, along with the carrying out of process of setting, thermograde diminishes gradually, when setting rate becomes large gradually, when the maximum local condensate depression in solid-liquid interface forward position is higher than forming core condensate depression, likely causes forming core and grow up forming tiny equiax crystal.If equiax crystal volume fraction is too small, equiax crystal can grown column crystal entrains into, and only has and when the volume fraction of equiax crystal reaches certain value, will present equiax crystal growth, thereby blocked the growth of directed dendrite.No matter turn to dendrite or the existence of equiax crystal, all destroyed the duration of oriented freezing organization.In cladding tissue due to every one deck, all can produce and turn to dendrite district, if after in forming process a cladding layer can not by last cladding layer turn to the complete remelting in dendrite district (as shown in Figure 2), destroyed the continuity of extension oriented growth tissue.Therefore by understanding processing parameter to turning to the rule that affects of dendrite district height, formulate rational single crystal preparation parameter collocation, contribute to obtain interlayer without the directional freeze drip molding that turns to dendrite district.
Ni base alloy is face-centred cubic structure, and its preferred orientation is <100> direction.When the construction direction of model is identical with the crystalline orientation of base plate, when the crystalline orientation of base plate is [001] direction, direction of heat flow is consistent with [001] direction, and the dendritic growth in liquid molten bath will carry out along [001] direction.In the process of building, control heat input, control laser cladding forming parameter, will obtain the monocrystal material identical with the crystalline orientation of base plate or monocrystalline component.When the construction direction of model is different with the crystalline orientation of base plate, when the crystalline orientation of base plate is [100] direction, direction of heat flow [001] is different from [100] direction, and the dendritic growth in liquid molten bath will carry out along the angled direction of [001] direction.In the process of building, control heat input, control laser cladding forming parameter, although the dendritic growth direction in liquid molten bath is angled with [001] direction, its crystalline orientation is identical with the crystalline orientation of base plate, also can obtain monocrystal material or monocrystalline component.The performance index of the monocrystalline obtaining are by EBSD experimental verification.
Accompanying drawing explanation
Fig. 1 Rene80 oriented growth cylindrulite and single crystal alloy preparation and component manufacturing system figure;
In figure: 1, high energy beam current, 2, powder-feeding nozzle, 3, shielding gas carries, 4, fixture, 5, at the part of building, 6, nickel-base alloy substrate, 7, powder feeder, 8, platen.
The distribution schematic diagram of different zones in drip molding in Fig. 2 laser solid forming process
Fig. 3 has the drip molding microsturcture of different base plate crystalline orientations.Left figure, base plate crystalline orientation is (001) direction, the direction that is shaped is parallel to base plate crystalline orientation; Right figure, base plate crystalline orientation is (100) direction, the direction that is shaped is perpendicular to base plate crystalline orientation.Wherein a), b), c) be respectively the microsturcture figure apart from base plate different positions place
Fig. 4 has the vertical section microstructure of the drip molding of different base plate crystalline orientations; Left figure, base plate crystalline orientation is (001) direction, the direction that is shaped is parallel to base plate crystalline orientation; Right figure, base plate crystalline orientation is (100) direction, the direction that is shaped is perpendicular to base plate crystalline orientation;
Fig. 5 has the horizontal section microstructure of the drip molding of different base plate crystalline orientations; Left figure, base plate crystalline orientation is (001) direction, the direction that is shaped is parallel to base plate crystalline orientation; Right figure, base plate crystalline orientation is (100) direction, the direction that is shaped is perpendicular to base plate crystalline orientation;
Fig. 6 has the grain orientation figure (Orientation image maps OIM) of the drip molding of different base plate crystalline orientations; Left figure a, base plate crystalline orientation is (001) direction, the direction that is shaped is parallel to base plate crystalline orientation; Right figure b, base plate crystalline orientation is (100) direction, the direction that is shaped is perpendicular to base plate crystalline orientation; C) be the reversed pole figure of a) figure; E) be b) the reversed pole figure of figure; D) be reversed pole figure IPF
Fig. 7 has the vertical section utmost point figure of the drip molding of different base plate crystalline orientations; Left figure, base plate crystalline orientation is (001) direction, the direction that is shaped is parallel to base plate crystalline orientation; Right figure, base plate crystalline orientation is (100) direction, the direction that is shaped is perpendicular to base plate crystalline orientation
Embodiment
By the embodiment by enumerating, the present invention is further illustrated below.
The present invention is a kind of nickel based super alloy Rene80 oriented growth cylindrulite and single crystal alloy preparation and component manufacture method, described method, and described equipment comprises:
A. a high energy beam current is if laser beam, electron beam, beam-plasma etc. are as thermal source;
B. a directionally solidified superalloy substrate;
C. the powder conveying system of a set of conveying Rene80 powder: comprise powder feeder and powder-feeding nozzle; Wherein the function of powder-feeding nozzle comprises water-cooling system, plenum system, powder feed system etc.
Alloy preparation or part manufacture process all complete in atmosphere, and in part manufacture process, the protection in liquid molten bath only carries shielding gas to realize by powder-feeding nozzle to Reciprocity of Laser & Materials district conveying powder time;
Concrete grammar comprises the following steps,
The first step: granularity is put into powder feeder for-200 orders～+ 325 object Rene80 powder;
Second step: adopt gripping unit that the nickel-base alloy base plate of directional freeze is clamped, be placed on worktable;
The 3rd step: argon gas is passed in powder feeder in the carrier gas of carrying as powder and powder-feeding nozzle and exported as shielding gas;
The 4th step: first open supply gas, powder conveyer, then start high energy beam current.At this moment powder be continuously fed into the interaction area of laser and substrate and enter laser and molten bath that substrate interact to form in, high energy beam current light source is along the cad model section track scanning that will build part, by the Rene80 powder of synchronous transport, successively melt deposition is on the nickel-base alloy plate of directional freeze, and preparation has the Rene80 part of different shapes and the size of oriented growth columanar structure.
Embodiment 1:
(1) adopt laser beam continuous melting deposition to prepare oriented growth cylindrulite and single crystal alloy
Testing selected base plate is Rene142 directionally solidified superalloy, and base plate thickness is 2mm.The laser process equipment of selecting is CO
2laser apparatus (peak power output is 6KW), optical maser wavelength is 1064nm, and the condenser lens focal length of selecting is 270mm, and focal spot radius is 0.69mm, and backplate surface is positioned at the focal plane of laser.
In part manufacturing processed, adopt base plate crystalline orientation to be parallel to part forming direction.First important parameter: laser power 600W is set, laser motion speed 200mm/min, powder feed rate 10g/m, shield gas flow rate 25L/min, carrier gas flux is 15L/min, z axial translation amount is 350um.Then open supply gas, powder conveyer, and start high energy beam current.At this moment powder is continuously fed into the interaction area of laser and substrate and enters laser and molten bath that substrate interact to form, by the motion of laser, the overlap joint in the overlap joint of cladding point, cladding road has formed Zhi Biqiang.
In Fig. 3-7, left figure is respectively the utmost point figure that adopts cross section, vertical section, horizontal section micro-organization chart and the vertical section of the straight wall wall part that Fig. 1 system manufactures.From the left figure of Fig. 3, can find out, in drip molding, the direction of growth of crystal grain is identical with the grain growing direction of base plate; In figure a), b) direction of growth of position place crystal grain is vertically upward, just at c) top of figure is that dendrite has appearred turning in straight wall coping.This explanation a), b) cladding layer of the position place laser dendrite that turns to that last layer is occurred all melts, thereby occurred the dendrite that the direction of growth is identical.In Fig. 4, left figure can further confirm the result shown in Fig. 3.In the left figure of Fig. 5, can find out that this orientation dendrite crystal grain is very evenly tiny.A) figure in Fig. 6 is the EBSD figure of left figure in Fig. 5, and the grain orientation that can find out this drip molding by this EBSD figure is identical.E) figure proves that this formation tissue is cubic texture, and tissue has good directional property.In the right figure of Fig. 7, can find out that the displacement angle between directed dendrite is less than 4 ° of left and right, displacement angle all can think monocrystalline at 10 ° with interior.
Embodiment 2:
(2) adopt laser beam continuous melting deposition to prepare oriented growth cylindrulite and single crystal alloy
Testing selected base plate is Rene142 directionally solidified superalloy, and weldment thickness is 2mm.The laser process equipment of selecting is CO
2laser apparatus (peak power output is 6KW), optical maser wavelength is 1064nm, and the condenser lens focal length of selecting is 270mm, and focal spot radius is 0.69mm, and backplate surface is positioned at the focal plane of laser.
In part manufacturing processed, adopt base plate crystalline orientation perpendicular to part forming direction.First important parameter: laser power 600W is set, laser motion speed 200mm/min, powder feed rate 10g/m, shield gas flow rate 25L/min, carrier gas flux is 15L/min, z axial translation amount is 350um.Then open supply gas, powder conveyer, and start high energy beam current.At this moment powder is continuously fed into the interaction area of laser and substrate and enters laser and molten bath that substrate interact to form, by the motion of laser, the overlap joint in the overlap joint of cladding point, cladding road has formed Zhi Biqiang.
In Fig. 3-7, right figure is respectively the utmost point figure that adopts cross section, vertical section, horizontal section micro-organization chart and the vertical section of the straight wall wall part that Fig. 1 system manufactures.From the right figure of Fig. 3, can find out, in drip molding, the direction of growth of crystal grain is vertical with the grain growing direction of base plate; In figure a), b) direction of growth of position place crystal grain is consistent, at c) there is turning to dendrite in figure place.This explanation a), b) cladding layer of the position place laser dendrite that turns to that last layer is occurred all melts, thereby occurred the dendrite that the direction of growth is identical.The direction of growth that in Fig. 4, right figure can find out crystal grain in drip molding the first layer is from the horizontal by-45 °, in the second layer, in the direction of growth of crystal grain and the first layer, the direction of growth direction of crystal grain is at 45 °, and the direction of growth of the direction of growth of the first layer crystal grain and second layer crystal grain is in 90 ° like this.In the left figure of Fig. 5, can find out that this orientation dendrite crystal grain is very evenly tiny.A) figure in Fig. 6 is the EBSD figure of left figure in Fig. 5, and the grain orientation that can find out this drip molding by this EBSD figure is identical, and some deflections occur the grain orientation at left side central portion place.E) figure proves that this formation tissue is cubic texture, and tissue has good directional property.In the right figure of Fig. 7, can find out that the displacement angle between directed dendrite is less than 9 ° of left and right, displacement angle larger may with the orientation of indivedual dendrite deflect relevant, but displacement angle all can think monocrystalline at 10 ° with interior.
Claims (2)
1. a nickel based super alloy Rene80 oriented growth cylindrulite and single crystal alloy preparation and method for manufacturing parts, it is characterized in that: described method is carried out in atmosphere, using high energy beam current as thermal source, the digital control system that moves through of high energy beam current has been controlled, the Rene80 flow of powder that carrier gas is carried melt deposition successively on the nickel-base alloy substrate of directional freeze, directly preparation has the alloy of the straight and upright columnar structure/monocrystalline of oriented growth, or directly manufactures the nickel based super alloy Rene80 part with the straight and upright columnar structure/monocrystalline of oriented growth, different cross section shape.
2. a kind of nickel based super alloy Rene80 oriented growth cylindrulite according to claim 1 and single crystal alloy are prepared and component manufacture method, it is characterized in that: the equipment of employing comprises:
A. a high energy beam current adopts laser beam, electron beam or beam-plasma as thermal source;
B. a directionally solidified superalloy substrate;
C. the powder conveying system of a set of conveying Rene80 powder: comprise powder feeder and powder-feeding nozzle; Wherein the function of powder-feeding nozzle comprises water-cooling system, plenum system, powder feed system;
Alloy preparation or part manufacture process all complete in atmosphere, and in part manufacture process, the protection in liquid molten bath only carries shielding gas to realize by powder-feeding nozzle to Reciprocity of Laser & Materials district conveying powder time;
Specifically comprise the following steps:
The first step: granularity is put into powder feeder for-200 orders～+ 325 object Rene80 powder;
Second step: adopt gripping unit that the nickel-base alloy base plate of directional freeze is clamped, be placed on worktable;
The 3rd step: argon gas is passed in powder feeder in the carrier gas of carrying as powder and powder-feeding nozzle and exported as shielding gas;
The 4th step: first open supply gas, powder conveyer, then start high energy beam current; At this moment powder be continuously fed into the interaction area of laser and substrate and enter laser and molten bath that substrate interact to form in, high energy beam current light source is along the cad model section track scanning that will build part, by the Rene80 powder of synchronous transport, successively melt deposition is on the nickel-base alloy plate of directional freeze, and preparation has the Rene80 part of different shapes and the size of oriented growth columanar structure;
In oriented growth cylindrulite and single crystal alloy preparation process, laser power, powder sending quantity, laser speed of feed have determined width and height, laser scanning strategy and the z axial translation amount of the heat input in laser processing procedure, single track cladding line; The scope of above-mentioned parameter is respectively: laser power: 400-1200W, powder sending quantity: 8-12g/ divides, laser speed of feed: 200-600mm/ divides, z axial translation amount: 100-500um/ time.
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Cited By (15)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104480465A (en) * | 2014-12-24 | 2015-04-01 | 上海交通大学 | Method for manufacturing nickel-based monocrystal high-temperature alloy component by utilizing laser cladding technology |
| CN104947175A (en) * | 2014-03-27 | 2015-09-30 | 中国科学院金属研究所 | Method for preparing single crystal high temperature alloy block material through laser 3D printing |
| CN105108142A (en) * | 2015-06-18 | 2015-12-02 | 航星利华(北京)科技有限公司 | Method for manufacturing monocrystalline and directional solidified part through laser 3D printer |
| CN105251999A (en) * | 2015-09-06 | 2016-01-20 | 航星利华(北京)科技有限公司 | Method for preparing rare earth reinforced equiaxial fine-crystal part through high-energy beam metal 3D printing |
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| CN106906382A (en) * | 2015-12-09 | 2017-06-30 | 通用电气公司 | Nickel based super alloy and its manufacture method |
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| CN111975006A (en) * | 2020-07-08 | 2020-11-24 | 北京航空航天大学 | Repair method of aircraft engine blade |
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Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002069507A (en) * | 2000-09-01 | 2002-03-08 | Hitachi Ltd | Method for manufacturing metal article, apparatus thereof, and laser beam condensing unit |
| CN1542173A (en) * | 2003-11-10 | 2004-11-03 | 北京航空航天大学 | Method for preparation of directional growth columnar crystal and monocrystal titanium alloy |
| CN1735714A (en) * | 2002-09-06 | 2006-02-15 | 阿尔斯通技术有限公司 | Method for controlling the microstructure of a laser metal formed hard layer |
-
2013
- 2013-09-21 CN CN201310430839.4A patent/CN103668461A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002069507A (en) * | 2000-09-01 | 2002-03-08 | Hitachi Ltd | Method for manufacturing metal article, apparatus thereof, and laser beam condensing unit |
| CN1735714A (en) * | 2002-09-06 | 2006-02-15 | 阿尔斯通技术有限公司 | Method for controlling the microstructure of a laser metal formed hard layer |
| CN1542173A (en) * | 2003-11-10 | 2004-11-03 | 北京航空航天大学 | Method for preparation of directional growth columnar crystal and monocrystal titanium alloy |
Non-Patent Citations (1)
| Title |
|---|
| 张冬云等: "工艺参数对 Rene80 激光定向凝固组影响研究", 《应用激光》, vol. 33, no. 2, 30 April 2013 (2013-04-30) * |
Cited By (23)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104947175A (en) * | 2014-03-27 | 2015-09-30 | 中国科学院金属研究所 | Method for preparing single crystal high temperature alloy block material through laser 3D printing |
| CN104480465A (en) * | 2014-12-24 | 2015-04-01 | 上海交通大学 | Method for manufacturing nickel-based monocrystal high-temperature alloy component by utilizing laser cladding technology |
| CN105108142A (en) * | 2015-06-18 | 2015-12-02 | 航星利华(北京)科技有限公司 | Method for manufacturing monocrystalline and directional solidified part through laser 3D printer |
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| US10801088B2 (en) | 2015-12-09 | 2020-10-13 | General Electric Company | Nickel base super alloys and methods of making the same |
| CN106906382A (en) * | 2015-12-09 | 2017-06-30 | 通用电气公司 | Nickel based super alloy and its manufacture method |
| CN106906382B (en) * | 2015-12-09 | 2019-05-14 | 通用电气公司 | Nickel based super alloy and its manufacturing method |
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| CN111339670A (en) * | 2020-02-28 | 2020-06-26 | 西安理工大学 | Dendritic crystal growth numerical simulation method in nickel-based alloy laser cladding process |
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| CN113681025A (en) * | 2021-07-21 | 2021-11-23 | 上海理工大学 | Method for preparing nickel-based alloy single crystal through additive manufacturing |
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