CN106077647A - A kind of laser gain material controls the method for fragility Laves phase during manufacturing nickel base superalloy - Google Patents
A kind of laser gain material controls the method for fragility Laves phase during manufacturing nickel base superalloy Download PDFInfo
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- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
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- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/20—Direct sintering or melting
- B22F10/25—Direct deposition of metal particles, e.g. direct metal deposition [DMD] or laser engineered net shaping [LENS]
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- B22F12/00—Apparatus or devices specially adapted for additive manufacturing; Auxiliary means for additive manufacturing; Combinations of additive manufacturing apparatus or devices with other processing apparatus or devices
- B22F12/40—Radiation means
- B22F12/41—Radiation means characterised by the type, e.g. laser or electron beam
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Abstract
The invention discloses a kind of method controlling fragility Laves phase during laser gain material manufactures nickel base superalloy.First laser gain material fabrication process parameters is carried out initial optimization, uses cooling medium to base material bottom coohng;Use laser modulation technique that light source is modulated again, it is thus achieved that more excellent Laser Modulation parameter, square wave: peak power: 600~1000W, pulse frequency: 10HZ~100HZ, dutycycle: 0.3~0.6;Sawtooth waveforms: crest 600~1200W, trough 0W, pulse frequency: 10HZ~100HZ;Sinusoidal wave parameter is: crest 600~1000W, trough 0W, pulse frequency: 10HZ~100HZ;Finally carry out nickel base superalloy laser gain material manufacture by above-mentioned parameter to shape, it is thus achieved that there is whole tiny equiaxed dendrite tissue and the formation of parts of fine discrete Laves phase.The present invention passes through laser modulation method, can effectively control laser gain material and manufacture the pick-up behavior of Laves phase during nickel base superalloy, reduce laser gain material and manufacture the cracking sensitivity of part, improve microscopic structure.
Description
Technical field
The present invention relates to laser metal material processing field, particularly relate to a kind of laser gain material and manufacture nickel base superalloy mistake
The method controlling fragility Laves phase in journey.
Background technology
Laser gain material manufacturing technology is a kind of technology combined with rapid prototyping by laser melting coating, owing to having material profit
It is widely used in the quick shaping of part, reparation and surface modification etc. by features such as high, with short production cycle, the low costs of rate.
Inconel 718 is a kind of precipitation strength type, containing Nb nickel base superalloy, because having good structure stability, solderability, height
The very good mechanical properties such as temperature intensity, fatigue at high temperature, croop property and high-temperature oxidation resistance and be widely used in aviation
The fields such as space flight, nuclear industry and energy source and power.It is exactly Nb element that laser gain material manufactures one of the most significant feature of nickel-base alloy
The interdendritic of segregation and Laves phase separates out.But, the formation of the brittle intermetallic thing Laves phase lastness to drip molding
Can be the most unfavorable.On the one hand, the precipitation of Laves phase can consume alloying element useful in matrix.On the other hand, fragility Laves
Provide forming core and the vantage point grown up for crackle mutually, can be the shape of crackle under residual stress or other outer load stress effects
Core and growth extension offer condition.The precipitation of Laves phase will cause the tensile property of drip molding, fracture toughness and fatigue behaviour to show
Write and decline.And, coarse long chain Laves phase manufactures the hot tearing sensitivity of Inconel 718 alloy by increasing laser gain material.
Therefore, it is necessary to control the pick-up behavior of Laves phase.
In recent decades, Chinese scholars is devoted to find the method effectively controlling Laves phase always.Qi et al. is by all
Homogenize Technology for Heating Processing and completely eliminate the Laves phase produced in laser gain material manufacture Inconel718 alloy.But, although high
Temperature homogenization heat treatment can eliminate as the effective method of one or reduce Laves phase, but will be Laves phased soln to
Determine degree, just inevitably lead to the appearance of some new problems, as there is recrystallization, grain coarsening and shaping after heat treatment
Part deformation etc..It is thus impossible to be completely dependent on subsequent heat treatment to process Laves phase problem, but by optimizing or improving processing
Technique itself controls the formation of Nb element segregation and Laves phase.It is concentrated mainly on currently, with respect to the research controlling Laves phase
Welding aspect.Radhakrishna et al. compares gas tungsten arc welding (GTA) and electron beam (EB) welding pool
Microscopic structure, finds that electro-beam welding process has a bigger cooldown rate, thus reduce interdendritic Nb element segregation and
The quantity of Laves phase.They are it was also found that reduce energy input in GTA welds, and the quantity of Laves phase will be suppressed.Ram
Et al. in GTA welding procedure, use pulse-current technique, find that diffusion region Nb element segregation alleviates, the Laves of netted link
Reducing mutually, aging response and stress crack significantly improve.Murthy etc. and GM Reddy etc. find to weld at 718 electron beams
Middle employing electron beam oscillation technology can effectively reduce Nb element segregation, and obtains discrete, tiny Laves phase.
Manikandan etc. find that control is welded fusion area Nb element segregation and the shape of Laves phase with recombination current pulse mode by helium
One-tenth is useful.Being formed by changing curing condition based on the studies above, Nb element segregation and Laves phase is to be suppressed
, as changed cooldown rate etc..
But, in laser gain material manufacture process, the research in terms of Nb element segregation and Laves phase control is more rare.
Dinda et al. have studied the impact on element segregation behavior of deposition path and scanning speed, finds deposition path and scanning speed
Element segregation behavior is not the most produced impact.Y.Chen et al. and Y.C.Zhang et al. have studied base material respectively and continues water-cooled
And the impact that liquid nitrogen cooling is on laser deposition 718 alloy microscopic structure, find that improving base material cooldown rate can reduce Nb element
Segregation and Laves phase are formed, but do not remove long chain Laves phase completely.
Summary of the invention
It is an object of the invention to provide a kind of laser gain material easy and simple to handle, that can quickly respond and manufacture nickel base superalloy
The control method of Laves phase.Detailed process is as follows:
S1, laser gain material fabrication process parameters is carried out initial optimization, it is thus achieved that elementary laser increases manufacture process window, excellent
Change parameter: average laser power is 300~800W, and scanning speed is 6~10mm/s, and powder sending quantity is 8-12g/min, spot diameter
It is 1~2mm, carrier gas flux 10~12L/min;
S2, laser gain material manufacture process use cooling medium cool down bottom base material, reduce in forming process
Heat accumulation;
S3, carry out nickel base superalloy laser gain material manufacture shape, LASER Light Source waveform modulated be square wave, sawtooth waveforms or
Sinusoidal wave;Wherein, the parameter of square wave is: peak power: 600~1000W, pulse frequency: 10HZ~100HZ, dutycycle: 0.3
~0.6;Sawtooth waveforms parameter is: crest 600~1200W, trough 0W, pulse frequency: 10HZ~100HZ;Sinusoidal wave parameter is:
Crest 600~1000W, trough 0W, pulse frequency: 10HZ~100HZ;Acquisition has whole tiny equiaxed dendrite tissue and tiny
Discrete Laves phase, thus reduce laser gain material and manufacture the cracking sensitivity of part, improve microscopic structure.
In described step S1, the laser gain material manufacture method used is: coaxial powder-feeding formula laser gain material manufacture method, or
Lateral powder feeding formula laser gain material manufacture method.
In described step S2, described cooling medium is tap water, deionized water or liquid nitrogen.
In described step S2, described base material is carbon steel, rustless steel or nickel-base alloy.
In described step S3, use color comparator pyrometer that bath temperature is measured, and the temperature data gathered is entered
Row computational analysis, the measurement of bath temperature and the concrete steps of data computational analysis include:
S3.1, being fixed two color comparator pyrometers, one of them pyrometer is from one-point measurement molten bath, sample side temperature
Degree, another thermometer follows the motion of first of laser melting coating, the change of synchro measure molten bath transient temperature;
S3.2, color comparator pyrometer probe hot spot and the position correction at center, molten bath, color comparator pyrometer and laser melting coating head axle
To in 15 degree of angles, and two color comparator pyrometer hot spots are less than the width of single track sedimentary;
S3.3, collection analysis temperature data, pyrometer frequency acquisition is designed as 1ms, after temperature acquisition completes, to temperature
Data carry out smooth treatment, and the curve processed is carried out derivation, it is thus achieved that the cooldown rate of weld pool surface.
One aspect of the present invention can be greatly improved the cooldown rate in molten bath and (can reach 106~107DEG C/s), significantly improve
Molten bath is supercool;On the other hand, periodic energy input will result in molten bath and the most quickly heats and quickly cool down.This two side
The factor in face is incited somebody to action, and promotes the forming core of crystal grain;Thinning solidification structure;Suppression Nb element segregation, reduces Laves phase and is formed, and then obtain
Obtain low volume fraction and tiny, the Laves phase granule of Discrete Distribution.The present invention not only solves laser gain material and manufactures nickel-base high-temperature
The hot tearing problem caused owing to fragility long chain Laves phase is formed in alloy process, and can effectively reduce useful alloy
Element segregation, thus reduce laser gain material and manufacture the cracking sensitivity of part, improve microscopic structure.
Accompanying drawing explanation
Fig. 1 uses conventional laser to increase the metallographic structure figure that material manufacture obtains;
Fig. 2 uses the metallographic structure figure that laser modulation method of the present invention obtains;
Fig. 3 uses conventional laser to increase the SEM figure that material manufacture obtains;
Fig. 4 uses the SEM figure that laser modulation method of the present invention obtains.
Below in conjunction with Figure of description and specific embodiment, the present invention is described in further detail.
Detailed description of the invention
Embodiment 1
S1, laser gain material fabrication process parameters is carried out initial optimization, it is thus achieved that elementary laser increases manufacture process window, excellent
Change parameter: average laser power is 400W, and scanning speed is 6mm/s, and powder sending quantity is 8g/min, and spot diameter is 1~2mm, carry
Throughput 10L/min;
S2, employing tap water cool down bottom nickel based substrate, reduce the heat accumulation in forming process;
S3, carry out nickel base superalloy laser gain material manufacture shape, LASER Light Source control select square wave, the parameter of square wave
For: peak power: 600W, pulse frequency: 10HZ~100HZ, dutycycle: 0.6.
Fig. 2 is the metallographic structure figure using laser modulation method of the present invention to obtain;As can be seen from Figure 2 metallographic structure by
The shaft-like dendrite composition such as tiny;Fig. 1 use conventional laser increase the metallographic structure of material manufacture acquisition by thick columnar dendrite
Composition.Fig. 4 is the SEM figure using laser modulation method of the present invention to obtain, Laves phase fine discrete pattern, and uses in Fig. 3 and pass
The Laves phase that system laser gain material manufacture obtains is thick long chain, illustrates the effectiveness of control method of the present invention.
Use color comparator pyrometer that bath temperature is measured, and the temperature data gathered is analyzed and cooldown rate
Calculate.The measurement of bath temperature and the concrete steps of process include:
S3.1, being fixed two color comparator pyrometers, one of them pyrometer is from one-point measurement molten bath, sample side temperature
Degree, another thermometer follows the motion of first of laser melting coating, the change of synchro measure molten bath transient temperature;
S3.2, color comparator pyrometer probe hot spot and the position correction at center, molten bath, color comparator pyrometer and laser melting coating head axle
To in 15 degree of angles, and two color comparator pyrometer hot spots are less than the width of single track sedimentary;
S3.3, collection analysis temperature data, pyrometer frequency acquisition is designed as 1ms, after temperature acquisition completes, to temperature
Data carry out smooth treatment, and the curve processed is carried out derivation, it is thus achieved that the cooldown rate of weld pool surface.
Embodiment 2
S1, laser gain material fabrication process parameters is carried out initial optimization, it is thus achieved that elementary laser increases manufacture process window, excellent
Change parameter: average laser power is 400W, and scanning speed is 10mm/s, and powder sending quantity is 12g/min, and spot diameter is 1~2mm,
Carrier gas flux 12L/min;
S2, employing go tap water to cool down bottom nickel based substrate, reduce the heat accumulation in forming process;
S3, carry out nickel base superalloy laser gain material manufacture shape, LASER Light Source control select sawtooth waveforms, sawtooth waveforms join
Number is: crest 900W, trough 0W, pulse frequency: 90HZ.
Embodiment 3:
S1, laser gain material fabrication process parameters is carried out initial optimization, it is thus achieved that elementary laser increases manufacture process window, excellent
Change parameter: average laser power is 600W, and scanning speed is 8mm/s, and powder sending quantity is 10g/min, and spot diameter is 1mm, carrier gas
Flow 10L/min;
S2, employing liquid nitrogen cool down bottom nickel based substrate, reduce the heat accumulation in forming process;
S3, the laser gain material manufacture carrying out nickel base superalloy shape, and LASER Light Source controls to select sine wave, sinusoidal wave
Parameter is: crest 700W, trough 0W, pulse frequency: 30HZ.
Claims (5)
1. the method that a laser gain material controls fragility Laves phase during manufacturing nickel base superalloy, it is characterised in that include
Following steps:
S1, laser gain material fabrication process parameters is carried out initial optimization, it is thus achieved that elementary laser increases manufacture process window, optimize ginseng
Number: average laser power is 300~800W, and scanning speed is 6~10mm/s, and powder sending quantity is 8-12g/min, and spot diameter is 1
~2mm, carrier gas flux 10~12L/min;
S2, laser gain material manufacture process use cooling medium cool down bottom base material, reduce the heat in forming process and amass
Tired;
S3, carry out nickel base superalloy laser gain material manufacture shape, LASER Light Source waveform modulated is square wave, sawtooth waveforms or sine
Ripple;Wherein, the parameter of square wave is: peak power: 600~1000W, pulse frequency: 10HZ~100HZ, dutycycle: 0.3~
0.6;Sawtooth waveforms parameter is: crest 600~1200W, trough 0W, pulse frequency: 10HZ~100HZ;Sinusoidal wave parameter is: ripple
Peak 600~1000W, trough 0W, pulse frequency: 10HZ~100HZ;Acquisition have whole tiny equiaxed dendrite tissue and tiny from
The Laves phase dissipated, thus reduce laser gain material and manufacture the cracking sensitivity of part, improve microscopic structure.
A kind of laser gain material the most according to claim 1 controls fragility Laves phase during manufacturing nickel base superalloy
Method, it is characterised in that: in step sl, the laser gain material manufacture method used is: coaxial powder-feeding formula laser gain material manufactures
Method, or lateral powder feeding formula laser gain material manufacture method.
A kind of laser gain material the most according to claim 1 controls fragility Laves phase during manufacturing nickel base superalloy
Method, it is characterised in that: in step s 2, described cooling medium is tap water, deionized water or liquid nitrogen.
A kind of laser gain material the most according to claim 1 controls fragility Laves phase during manufacturing nickel base superalloy
Method, it is characterised in that: in step s 2, described base material is carbon steel, rustless steel or nickel-base alloy.
A kind of laser gain material the most according to claim 1 controls fragility Laves phase during manufacturing nickel base superalloy
Method, it is characterised in that: in step s3, use color comparator pyrometer that bath temperature is measured, and to the temperature number gathered
According to carrying out computational analysis, the measurement of bath temperature and the concrete steps of data computational analysis include:
S3.1, being fixed two color comparator pyrometers, one of them pyrometer is from sample side one-point measurement bath temperature, separately
One thermometer follows the motion of first of laser melting coating, and synchro measure molten bath transient temperature changes;
The position correction at S3.2, color comparator pyrometer probe hot spot and center, molten bath, color comparator pyrometer and laser melting coating head axially in
15 degree of angles, and two color comparator pyrometer hot spots are less than the width of single track sedimentary;
S3.3, collection analysis temperature data, pyrometer frequency acquisition is designed as 1ms, after temperature acquisition completes, to temperature data
Carry out smooth treatment, and the curve processed is carried out derivation, it is thus achieved that the cooldown rate of weld pool surface.
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Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP2840154A1 (en) * | 2013-08-21 | 2015-02-25 | MTU Aero Engines GmbH | Method for producing components from and with laves phases |
CN104493152A (en) * | 2014-12-03 | 2015-04-08 | 沈阳工业大学 | Powder used for laser-cladding zinc corrosion resistant cobalt-based alloy and preparation technology for modified layer |
CN105506615A (en) * | 2015-12-11 | 2016-04-20 | 上海交通大学 | Method for controlling microstructure and hot crack sensibility of laser cladding coating |
CN105543747A (en) * | 2015-12-21 | 2016-05-04 | 西北工业大学 | Preparation method of material increase manufactured nickel-based high-temperature alloy reserved with Laves phase |
CN105695986A (en) * | 2016-02-25 | 2016-06-22 | 上海交通大学 | System and method for repairing nickel-based monocrystal high-temperature alloy turbine blade tip |
-
2016
- 2016-07-27 CN CN201610604775.9A patent/CN106077647B/en not_active Expired - Fee Related
Patent Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP2840154A1 (en) * | 2013-08-21 | 2015-02-25 | MTU Aero Engines GmbH | Method for producing components from and with laves phases |
CN104493152A (en) * | 2014-12-03 | 2015-04-08 | 沈阳工业大学 | Powder used for laser-cladding zinc corrosion resistant cobalt-based alloy and preparation technology for modified layer |
CN105506615A (en) * | 2015-12-11 | 2016-04-20 | 上海交通大学 | Method for controlling microstructure and hot crack sensibility of laser cladding coating |
CN105543747A (en) * | 2015-12-21 | 2016-05-04 | 西北工业大学 | Preparation method of material increase manufactured nickel-based high-temperature alloy reserved with Laves phase |
CN105695986A (en) * | 2016-02-25 | 2016-06-22 | 上海交通大学 | System and method for repairing nickel-based monocrystal high-temperature alloy turbine blade tip |
Non-Patent Citations (3)
Title |
---|
刘洪刚等: "冷却速率对激光熔覆高温合金涂层组织的影响", 《机械工程材料》 * |
张尧成: "激光熔覆INCONEL718 合金涂层的成分偏聚与强化机理研究", 《中国博士学位论文全文数据库工程科技Ⅰ辑》 * |
龙怡彤等: "激光熔覆Inconel718合金铌偏聚(英文)", 《中国有色金属学报(英文版)》 * |
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