CN1542173A - Method for preparation of directional growth columnar crystal and monocrystal titanium alloy - Google Patents
Method for preparation of directional growth columnar crystal and monocrystal titanium alloy Download PDFInfo
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- CN1542173A CN1542173A CNA2003101134202A CN200310113420A CN1542173A CN 1542173 A CN1542173 A CN 1542173A CN A2003101134202 A CNA2003101134202 A CN A2003101134202A CN 200310113420 A CN200310113420 A CN 200310113420A CN 1542173 A CN1542173 A CN 1542173A
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Abstract
The preparation process of epitaxially growing cylindrulite and monocrystal titanium alloy is that inside dynamically sealed protecting chamber with adjustable atmosphere, the high-energy beam flow as heat source conveys titanium alloy powder flow is molten and deposited onto common titanium alloy base board continuously or one layer by one layer so as to grow epitaxially erect cylindrulite structure, titanium alloy ingot with different cross sections or complicated titanium alloy part via no-mold free formation. Thus prepared titanium alloy material may be used as key high temperature structural member of equipment widely used in petroleum, marine, aviation, space and other fields.
Description
Technical field
The present invention relates to a kind of preparation method of titanium alloy material, be meant particularly a kind of employing to titanium alloy powder stream continuous melting deposition or successively melt deposition, directly free forming has the titanium alloy ingot of oriented growth cylindrulite and single crystal organization and the preparation method of part under noncontact, no mould, inert atmosphere conditions.
Background technology
Outstanding properties advantages such as titanium alloy has that density is low, intensity is high, yield tensile ratio is high, solidity to corrosion and mechanical behavior under high temperature excellence are widely used as crucial thermal structure spare in industrial machineries such as petrochemical industry, ocean, Aeronautics and Astronautics, naval vessels, metallurgy, weapons equipment.Along with improving constantly of industrial technology level, more and more harsh to the requirement of high-temperature titanium alloy material property and technology of preparing thereof.
The main method that improves the high-temperature titanium alloy mechanical behavior under high temperature at present is that near is carried out solution strengthening, control β transformation tissue and utilizes little metal silicide precipitation strength.But owing to be subjected to the decisive influence of titanium alloy person's character, adopt above-mentioned traditional metal materials enhancement method and improve the long term high temperature mechanical property that the alloy composition method improves high-temperature titanium alloy, progress is not extremely slowly, make substantial progress for a long time both at home and abroad over nearly 20 years.
Crystal boundary is that structural metallic materialss such as titanium alloy are out of shape under the Long-term Service under High Temperature condition, the weak link of crack initiation and expansion, especially under the hot conditions Sauerstoffatom to the inner rapid osmotic diffusion of titanium alloy and and then cause serious crystal boundary fragility, the rapid passage that oxygen diffusion layer fragility and part early fracture lost efficacy, therefore, if can eliminate in the component of the crucial hot junction of high-temperature titanium alloy perpendicular to the crystal boundary that is subjected to force direction (being horizontal crystal boundary), prepare the titanium alloy material with the straight and upright cylindrulite of oriented growth, the mechanical behavior under high temperature of titanium alloy component is high-temperature duration life especially, high temperature mechanical properties such as creep strength will increase substantially undoubtedly.If can eliminate this weak link of crystal boundary fully, prepare the monocrystalline titanium alloy, the performance of titanium alloy component then has more significantly and improves.Yet because the height chemical activity of titanium under the high temperature, serious chemical reaction almost can take place with all high-temperature refractory formworks in the high-temperature titanium alloy melt in the directional freeze process; Because the thermal conductivity of titanium alloy is very low, solidification cooling is slow, be difficult to stably to set up and to keep required speed of cooling of directional freeze and high thermograde along the direction of growth in the liquid-solid interface forward position, melts of titanium alloy will be mainly by the heat radiation of type wall in its vicinity a large amount of forming cores in zone finally grow up and be equiax crystal, so all metallic substance directional solidification techniques all can't be realized the oriented growth of titanium alloy now, there be not the research and the bibliographical information of any relevant titanium alloy directional solidification technique and oriented growth cylindrulite or monocrystalline titanium alloy material both at home and abroad yet.
Summary of the invention
The objective of the invention is, provide the high energy beam current continuous melting deposition of oriented growth cylindrulite and monocrystalline titanium alloy and ingot and part or successively the titanium alloy of melt deposition do not have mould free forming novel preparation method.This method can be prepared different shape titanium alloy ingot and the various complicated near-purification formation of parts with the straight and upright cylindrulite of oriented growth and single crystal organization feature, its mechanical behavior under high temperature especially high temperature such as high temperature creep property, high-temperature duration life mechanical property increases substantially than industry forging and casting equiax crystal titanium alloy, can be widely used in the industry such as petrochemical industry, ocean, Aeronautics and Astronautics, naval vessels, metallurgy, weapons.
The preparation method of titanium alloy of the present invention is achieved in that in dynamic seal atmosphere controlled processing protection chamber or the controlled processing protection chamber of closed atmosphere (vacuumize earlier and afterwards fill inert protective gas), with high energy beam current as thermal source, with the titanium alloy powder of air-flow or gravity synchronous transport stream continuous melting deposition or melt deposition successively on the common alloy of titanium substrate, no mould free forming directly preparation has the titanium alloy ingot of the straight and upright columnar structure of oriented growth, different cross section shape or the titanium alloy component of complexity arbitrarily; Adopt the means of choosing crystalline substance or use single crystal seed, the continuous melting deposition can be prepared monocrystalline titanium alloy ingot, and successively melt deposition also can be prepared the monocrystalline titanium alloy component on the monocrystalline titanium alloy substrate.
The preparation method of described titanium alloy, its equipment comprises,
(A) titanium alloy substrate;
(B) a dynamic seal atmosphere controlled processing protection chamber or the controlled Processing Room of closed atmosphere;
(C) high energy beam current is as thermal source;
(D) powder conveying system of a conveying titanium alloy powder,
This method comprises the following steps,
The first step: with granularity is that-60～+ 300 purpose titanium alloy powders are put into powder feeder;
Second step: titanium alloy substrate is put into the controlled processing of dynamic seal atmosphere protection chamber or closed atmosphere controlled processing protection chamber and tighten up;
The 3rd step: with purity is that 99.99～99.999% high-purity argon gas or helium inert protective gas charge in the controlled processing protection of the dynamic seal atmosphere chamber or with the controlled processing protection of closed atmosphere chamber elder generation suction to 10
-1～10
-3It is that 99.99～99.999% high-purity argon gas or helium inert protective gas are to normal pressure that Pa charges into purity again;
The 4th step: import the high energy beam current thermal source, open powder feeder synchronously and carry titanium alloy powder, require the titanium alloy substrate surface and the calmodulin binding domain CaM surface local of formation of parts or ingot to be melted, wherein thermal source is according to the parameters such as its power of shape size adjustment, bundle shape of spot and beam spot size of required preparation titanium alloy component or ingot, the powder transfer rate is according to the requirements such as shape size of preparation part and ingot, and is suitable with high energy beam power, beam spot size, sweep velocity, monolayer deposition height, continuous pulling speed (being that the continuous melting deposition increases speed) etc.;
The 5th step: shaping ingot or part process, by the continuous lifting (substrate is motionless) of high energy beam current thermal source processing head or drop-down continuously (the thermal source processing head is motionless) of substrate, the high energy beam current thermal source is deposited on the titanium alloy powder continuous melting of synchronous transport on the common alloy of titanium substrate, and preparation has the titanium alloy ingot of directional freeze columanar structure; Utilize the high energy beam current thermal source with the titanium alloy powder of synchronous transport continuously or layer by layer deposition on titanium alloy single crystal seed or single crystal substrate, preparation has the titanium alloy ingot or the complicated shape of single crystal organization; Or the high energy beam current light source is along part C AD model cross sectional slice track scanning, and successively melt deposition is on the common alloy of titanium substrate with the titanium alloy powder of synchronous transport, and preparation has the titanium alloy component of the different shapes and the size of directional freeze columanar structure;
The 6th step: after the directional freeze column crystal of preparation or monocrystalline titanium alloy component or ingot are cooled to below 100 ℃, open dynamic seal atmosphere controlled processing protection chamber or the controlled processing protection of closed atmosphere chamber, with its taking-up;
The 7th step: as required, directional freeze column crystal or monocrystalline titanium alloy component or the ingot of preparation carried out composition, tissue and performance test.
The advantage of titanium alloys Preparation Method of the present invention is:
Prepared titanium alloy ingot and part have straight and upright column crystal of oriented growth and single crystal organization, thereby has excellent mechanical behavior under high temperature, especially the long-term structure stability of high temperature such as high-temperature duration life, creep strength mechanical property and high temperature is compared forging and is cast the equiax crystal titanium alloy material and increases substantially, also has excellent room-temperature mechanical property simultaneously, its intensity reaches forged titanium alloy level, and plasticity is significantly higher than the forged titanium alloy.
Do not need mould in the preparation process, the high energy beam current that uses high-energy-density with titanium alloy powder melt fast, rapid solidification, can set up and keep high thermograde in the liquid-solid interface forward position along the direction of growth, realize titanium alloy crystalline oriented growth, thereby can prepare titanium alloy ingot and complicated shape with straight and upright oriented growth column crystal and monocrystalline;
This preparation method can effectively protect titanium alloy, effectively prevent titanium alloy oxidation, air-breathing;
This preparation method also can shorten the titanium alloy component manufacturing cycle significantly, reduces manufacturing cost, improve material use efficiency.
Description of drawings
Fig. 1 is the synoptic diagram that the continuous melting depositional mode prepares oriented growth titanium alloy cylindrulite bar.
Fig. 2 is that successively the melt deposition mode prepares the synoptic diagram of oriented growth cylindrulite titanium alloy plate.
Fig. 3 adopts the continuous melting depositional mode to prepare the synoptic diagram of oriented growth monocrystalline titanium alloy ingot on single crystal seed.
Fig. 4 adopts laser beam continuous melting deposition preparation oriented growth cylindrulite titanium alloy cylinder bar photo in kind.
Fig. 5 is the microstructure picture at optical metallographic microscope analysis chart 4 bars.
Fig. 6 be adopt laser beam successively melt deposition prepare the tabular ingot of oriented growth cylindrulite titanium alloy thin wall photo in kind.
Fig. 7 is the microstructure picture at optical metallographic microscope analysis chart 6 sheet materials.
Fig. 8 be adopt laser beam successively melt deposition prepare oriented growth cylindrulite titanium alloy component photo in kind.
Among the figure: 1. the controlled processing protection of 2. powder feeder nozzles, 3. dynamic seals of high energy beam current thermal source or closed atmosphere chamber 4. substrates, 5. titanium alloy powders flow 6. bars, 7. sheet materials, 8. single crystal seed substrates, 9. monocrystalline titanium alloy ingots
Embodiment
Below will the present invention is further illustrated by listed examples.
The present invention is the preparation method of a kind of oriented growth cylindrulite and monocrystalline titanium alloy, and described equipment comprises,
(A) titanium alloy substrate;
(B) a dynamic seal atmosphere controlled processing protection chamber or the controlled Processing Room of closed atmosphere;
(C) high energy beam current is as thermal source;
(D) powder conveying system of a conveying titanium alloy powder,
This method comprises the following steps,
The first step: with granularity is that-60～+ 300 purpose titanium alloy powders are put into powder feeder;
Second step: titanium alloy substrate is put into the controlled processing of dynamic seal atmosphere protection chamber or closed atmosphere controlled processing protection chamber and tighten up;
The 3rd step: with purity is that 99.99～99.999% high-purity argon gas or helium inert protective gas charge in the controlled processing protection of the dynamic seal atmosphere chamber or with the controlled processing protection of closed atmosphere chamber elder generation suction to 10
-1～10
-3It is that 99.99～99.999% high-purity argon gas or helium inert protective gas are to normal pressure that Pa charges into purity again;
The 4th step: import the high energy beam current thermal source, open powder feeder synchronously and carry titanium alloy powder, require the titanium alloy substrate surface and the calmodulin binding domain CaM surface local of formation of parts or ingot to be melted, wherein thermal source is according to the parameters such as its power of shape size adjustment, bundle shape of spot and beam spot size of required preparation titanium alloy component or ingot, the powder transfer rate is according to the requirements such as shape size of preparation part and ingot, and is suitable with high energy beam power, beam spot size, sweep velocity, monolayer deposition height, continuous pulling speed (being that the continuous melting deposition increases speed) etc.;
The 5th step: shaping ingot or part process, by the continuous lifting (substrate is motionless) of high energy beam processing head or drop-down continuously (the thermal source processing head is motionless) of substrate, the high energy beam current thermal source is deposited on the titanium alloy powder continuous melting of synchronous transport on the common alloy of titanium substrate, and preparation has the titanium alloy ingot of directional freeze columanar structure; Utilize the high energy beam current thermal source with the titanium alloy powder of synchronous transport continuously or layer by layer deposition on titanium alloy single crystal seed or single crystal substrate, preparation has the titanium alloy ingot or the complicated shape of single crystal organization; Or the high energy beam current light source is along part C AD model cross sectional slice track scanning, and successively melt deposition is on the common alloy of titanium substrate with the titanium alloy powder of synchronous transport, and preparation has the titanium alloy component of the different shapes and the size of directional freeze columanar structure;
The 6th step: after the directional freeze column crystal of preparation or monocrystalline titanium alloy component or ingot are cooled to below 100 ℃, open dynamic seal atmosphere controlled processing protection chamber or the controlled processing protection of closed atmosphere chamber, with its taking-up;
The 7th step: as required, directional freeze column crystal or monocrystalline titanium alloy component or the ingot of preparation carried out composition, tissue and performance test.
Embodiment 1
(1) adopts laser beam continuous melting deposition preparation oriented growth cylindrulite titanium alloy cylinder bar
On flowing over continuous CO 2 laser materials processing suite of equipment, the 5kW that is furnished with three-shaft linkage 4-coordinate CNC laser processing machine bed carries out the bar preparation research; select for use hot rolling alpha+beta diphasic titanium alloy BT9 as substrate; its nominal chemical ingredients is Ti-6.4%Al-3.3%Mo-1.6%Zr-0.27%Si by weight percentage; selecting the argon gas atomized particle size for use is the starting material of-100～+ 200 purpose Ti-6Al-4V spherical powders as laser fast forming; selecting purity for use is that 99.999% high-purity argon gas is as shielding gas and powder delivering gas; the laser fast forming processing parameter is: the about 5mm of laser beam spot diameter; laser power 2.4～2.5kW; the continuous pulling speed of laser beam (being that the continuous melting deposition increases speed) is about 7～8mm/min; the powder feeding rate is about 6g/min; in the controlled processing protection of dynamic seal atmosphere chamber; the continuous melting deposition is prepared the about 13～15mm elongate cylinder of diameter bar, and it is shown in Figure 4 to see also photo in kind.
Adopt the chemical composition change of chemical analysis method Accurate Analysis laser forming front and back titanium alloy, the result is as shown in table 1, show that the titanium alloy main alloy element is almost without any variation in the laser deposition forming process, alloying element does not have scaling loss, and alloy oxygen level and nitrogen content are all lower.
Table 1 laser beam continuous melting depositing Ti-6Al-4V titanium alloy rod bar chemical composition analysis result
| Sample | ??Ti | ??Al | ??V | ??O | ??N | ??C | ??H | ??Fe | ??Si |
| Starting powder | Surplus | 6.28 | ?2.16 | ?0.091 | 0.0078 | ?0.012 | 0.0082 | ?0.065 | ?0.034 |
| The laser forming bar | Surplus | 6.17 | ?2.14 | ?0.14 | ?0.012 | ?0.039 | 0.0028 | ?0.068 | ?0.036 |
Adopt optical metallographic microscope to analyze the microstructure of this titanium alloy rod bar, as shown in Figure 5, can obviously observe the tissue signature of the straight and upright column crystal of oriented growth, and dense structure, pore-free, nothing are mingled with, flawless.
Adopt 5 times of bar-shaped tension specimens of standard (gauge length diameter 5mm) on MTS-880 multifunctional material mechanics Performance Test System, estimate the room-temperature mechanical property of the bar-shaped Ti-6Al-4V titanium alloy of this kind, mechanical property test result shown in the table 2 shows: forge the Ti-6Al-4V titanium alloy with industry and compare, laser beam successive sedimentation Ti-6Al-4V titanium alloy has excellent mechanical property, its intensity reaches forged titanium alloy level, and its plasticity is significantly higher than the forged titanium alloy.
Table 2 laser beam continuous melting depositing Ti-6Al-4V titanium alloy rod bar room temperature tensile mechanical property test result
| Specimen coding | Yield strength σ s(MPa) | Tensile strength sigma b(MPa) | Relative reduction in area ψ (%) | Unit elongation δ (%) |
| ????12-1 | ????923.0 | ????934.5 | ????15.7 | ????10.6 |
| ????12-2 | ????913.2 | ????927.8 | ????19.3 | ????8.0 |
| ????13-1 | ????904.7 | ????907.0 | ????22.7 | ????10.6 |
| ????13-2 | ????893.3 | ????905.7 | ????23.1 | ????14.9 |
| ????14-1 | ????864.5 | ????899.2 | ????26.6 | ????11.7 |
| ????14-2 | ????906.0 | ????923.5 | ????20.3 | ????13.0 |
(2) adopt laser beam successively melt deposition prepare oriented growth cylindrulite titanium alloy plate
Is being furnished with the enterprising andante material of the 5kW crossing current continuous CO 2 laser materials processing suite of equipment preparation research of three-shaft linkage 4-coordinate CNC laser processing machine bed; select for use hot rolling alpha+beta diphasic titanium alloy BT9 as substrate; its nominal chemical ingredients is Ti-6.4%Al-3.3%Mo-1.6%Zr-0.27%Si by weight percentage; selecting the argon gas atomized particle size for use is the starting material of-100～+ 200 purpose Ti-6Al-4V spherical powders as laser fast forming; selecting purity for use is that 99.999% high-purity argon gas is as shielding gas and powder delivering gas; the laser fast forming processing parameter is: the about 4mm of laser beam spot diameter; laser power 2.6～2.7kW; about 300～the 390mm/min of sweep velocity; monolayer deposition increases the about 0.5～0.7mm of speed; the powder feeding rate is about 7g/min; in the controlled processing protection of dynamic seal atmosphere chamber; successively melt deposition is prepared the tabular ingot of thin-walled that thickness is 5～7mm, and it is shown in Figure 6 to see also photo in kind.
Adopt the chemical composition change of chemical analysis method Accurate Analysis laser forming front and back titanium alloy, the result is as shown in table 3, show that the titanium alloy main alloy element is almost without any variation in the laser deposition forming process, alloying element does not have scaling loss, and alloy oxygen level and nitrogen content are all lower.
Table 3 laser beam is melt deposition Ti-6Al-4V titanium alloy plate chemical composition analysis result successively
| Sample | ????Ti | ????Al | ????V | ????O | ????N | ????C | ????H | ????Fe | ????Si |
| Starting powder | Surplus | 6.28 | ?3.89 | ?0.14 | ?0.036 | ?0.018 | 0.0041 | ?0.094 | ??0.038 |
| Laser forming sheet material | Surplus | 6.09 | ?3.85 | ?0.16 | ?0.047 | ?0.030 | 0.0050 | ?0.10 | ??0.040 |
Analyze the microstructure of this titanium alloy plate with optical metallographic microscope, as shown in Figure 7, can significantly observe tissue signature, and dense structure, pore-free, nothing are mingled with, flawless with straight and upright oriented growth cylindrulite.
Adopt 5 times of bar-shaped tension specimens of standard (gauge length diameter 5mm) on MTS-880 multifunctional material mechanics Performance Test System, estimate the room-temperature mechanical property of the bar-shaped Ti-6Al-4V titanium alloy of this kind, mechanical property test result shown in the table 4 shows: forge the Ti-6Al-4V titanium alloy with industry and compare, laser beam successive sedimentation Ti-6Al-4V titanium alloy has excellent mechanical property, its intensity reaches forged titanium alloy level, and its plasticity is significantly higher than the forged titanium alloy.
Table 4 laser beam successive sedimentation Ti-6Al-4V titanium alloy plate room temperature tensile mechanical property test result
| Specimen coding | Annealed state | Modulus (GPa) | Yield strength σ s(MPa) | Tensile strength sigma b(MPa) | Relative reduction in area ψ (%) | Unit elongation δ (%) |
| ????11 | ????√ | ????111.8 | ????786.8 | ????855.9 | ????29.0 | ????22.2 |
| ????12 | ????√ | ????116.0 | ????805.9 | ????871.8 | ????30.6 | ????22.4 |
| ????13 | ????√ | ????115.1 | ????818.4 | ????892.2 | ????28.0 | ????18.8 |
| ????14 | ????√ | ????116.2 | ????816.3 | ????890.4 | ????28.7 | ????18.8 |
| ????15 | ????√ | ????112.5 | ????809.0 | ????882.1 | ????33.9 | ????13.2 |
(3) adopt laser beam CAD section track scanning successively melt deposition prepare oriented growth cylindrulite titanium alloy component
At the 5kW that the is furnished with three-shaft linkage 4-coordinate CNC laser processing machine bed continuous CO that flows over
2Carry out the part preparation research on the Materialbearbeitung mit Laserlicht integrated system; select for use hot rolling alpha+beta diphasic titanium alloy BT9 as substrate; its nominal chemical ingredients is Ti-6.4%Al-3.3%Mo-1.6%Zr-0.27%Si by weight percentage; selecting the argon gas atomized particle size for use is the starting material of-100～+ 200 purpose Ti-6Al-4V spherical powders as laser fast forming; selecting purity for use is that 99.999% high-purity argon gas is as shielding gas and powder delivering gas; the laser fast forming processing parameter is: the about 3～4mm of laser beam spot diameter; laser power 2.7～2.8kW; the about 350mm/min of sweep velocity; the powder feeding rate is about 8g/min; in the controlled processing protection of dynamic seal atmosphere chamber; along part C AD section track scanning, successively melt deposition prepares the titanium alloy component blank.See also material object as shown in Figure 8.
Embodiment 2
Adopt beam-plasma continuous melting deposition preparation oriented growth cylindrulite titanium alloy cylinder bar
On the 30kW plasma suite of equipment that is equipped with digital-control processing system, carry out the bar preparation research; select for use hot rolling alpha+beta diphasic titanium alloy BT9 as substrate; its nominal chemical ingredients is Ti-6.4%Al-3.3%Mo-1.6%Zr-0.27%Si by weight percentage; selecting the argon gas atomized particle size for use is that-100～+ 200 purpose Ti-6Al-4V spherical powders are as starting material; selecting purity for use is that 99.999% high-purity argon gas is as shielding gas and powder delivering gas; processing parameter is: the about 15mm of nozzle bore; the continuous drop-down speed of substrate (being that the continuous melting deposition increases speed) is 12mm/min; the powder feeding rate is about 20g/min; in airtight protection chamber, the continuous melting deposition is prepared the cylinder bar of the about 20mm of diameter.
Adopt the cylindrical bar of electron beam continuous melting deposition preparation oriented growth cylindrulite titanium alloy
On 40kW electron beam suite of equipment, carry out the bar preparation research; select for use hot rolling alpha+beta diphasic titanium alloy BT9 as substrate; its nominal chemical ingredients is Ti-6.4%Al-3.3%Mo-1.6%Zr-0.27%Si by weight percentage; selecting the argon gas atomized particle size for use is that-100～+ 200 purpose Ti-6Al-4V spherical powders are as starting material; selecting purity for use is that 99.999% high-purity argon gas is as shielding gas and powder delivering gas; processing parameter is: voltage of supply 18kV; the about 20mm of beam spot diameter; the about 15mm/min of the continuous drop-down speed of substrate (being that the continuous melting deposition increases speed); the about 50g/min of powder feeding rate; in airtight protection chamber, the continuous melting deposition is prepared into the cylinder bar of the about 30mm of diameter.
Adopt tungsten argon arc continuous melting deposition preparation oriented growth cylindrulite titanium alloy cylinder bar
Tungsten electrode diameter phi 3.2mm; the 15kW tungsten argon arc welding gun of nozzle bore φ 3mm is as heat resource equipment; select for use hot rolling alpha+beta diphasic titanium alloy BT9 as substrate; its nominal chemical ingredients is Ti-6.4%Al-3.3%Mo-1.6%Zr-0.27%Si by weight percentage; selecting the argon gas atomized particle size for use is that-100～+ 200 purpose Ti-6Al-4V spherical powders are as starting material; selecting purity for use is that 99.999% high-purity argon gas is as shielding gas and powder delivering gas; processing parameter is: working current 180A; operating voltage 26V; it is 10mm/min that speed is increased in successive sedimentation; the about 15g/min of powder feeding rate; in the controlled processing protection of dynamic seal atmosphere chamber, the continuous melting deposition is prepared into the about 18～20mm cylinder of diameter bar.
Claims (10)
1, the preparation method of a kind of oriented growth cylindrulite and monocrystalline titanium alloy, it is characterized in that: described method is in dynamic seal atmosphere controlled processing protection chamber or airtight protection chamber (vacuumize earlier and afterwards fill inert protective gas), with high energy beam current as thermal source, with the titanium alloy powder of air-flow or gravity synchronous transport stream continuous melting deposition or melt deposition successively on the common alloy of titanium substrate, no mould free forming directly preparation has the titanium alloy ingot of the straight and upright columnar structure of oriented growth, different cross section shape or the titanium alloy component of complexity arbitrarily; Adopt the means of choosing crystalline substance or use seed crystal, the continuous melting deposition can be prepared monocrystalline titanium alloy ingot, and successively melt deposition also can be prepared the monocrystalline titanium alloy component on the monocrystalline titanium alloy substrate.
2, the preparation method of titanium alloy according to claim 1 is characterized in that: described equipment comprises,
(A) titanium alloy substrate;
(B) a dynamic seal atmosphere controlled processing protection chamber or the controlled Processing Room of closed atmosphere;
(C) high energy beam current is as thermal source;
(D) powder conveying system of a conveying titanium alloy powder,
This method comprises the following steps,
The first step: with granularity is that-60～+ 300 purpose titanium alloy powders are put into powder feeder;
Second step: titanium alloy substrate is put into the controlled processing of dynamic seal atmosphere protection chamber or closed atmosphere controlled processing protection chamber and tighten up;
The 3rd step: be that 99.99～99.999% high-purity argon gas or helium inert protective gas charge in the controlled processing protection of the dynamic seal atmosphere chamber or the controlled processing protection of closed atmosphere chamber elder generation suction is charged into purity again to 10-1～10-3Pa with purity be that 99.99～99.999% high-purity argon gas or helium inert protective gas are to normal pressure;
The 4th step: import the high energy beam current thermal source, open powder feeder synchronously and carry titanium alloy powder, require the titanium alloy substrate surface and the calmodulin binding domain CaM surface local of formation of parts or ingot to be melted, wherein thermal source is according to the parameters such as its power of shape size adjustment, bundle shape of spot and beam spot size of required preparation titanium alloy component or ingot, the powder transfer rate is according to the requirements such as shape size of preparation part and ingot, and is suitable with high energy beam power, beam spot size, sweep velocity, monolayer deposition height, continuous pulling speed (being that the continuous melting deposition increases speed) etc.;
The 5th step: shaping ingot or part process, by the continuous lifting (substrate is motionless) of high energy beam current thermal source processing head or drop-down continuously (the thermal source processing head is motionless) of substrate, the high energy beam current thermal source is deposited on the titanium alloy powder continuous melting of synchronous transport on the common alloy of titanium substrate, and preparation has the titanium alloy ingot of oriented growth columanar structure; Utilize the high energy beam current thermal source with the titanium alloy powder of synchronous transport continuously or layer by layer deposition on titanium alloy single crystal seed or single crystal substrate, preparation has the titanium alloy ingot or the complicated shape of single crystal organization; Or the high energy beam current light source is along part C AD model cross sectional slice track scanning, and successively melt deposition is on the common alloy of titanium substrate with the titanium alloy powder of synchronous transport, and preparation has the titanium alloy component of the different shapes and the size of oriented growth columanar structure;
The 6th step: after the oriented growth column crystal of preparation or monocrystalline titanium alloy component or ingot are cooled to below 100 ℃, open dynamic seal atmosphere controlled processing protection chamber or the controlled processing protection of closed atmosphere chamber, with its taking-up;
The 7th step: as required, oriented growth column crystal or monocrystalline titanium alloy component or the ingot of preparation carried out composition, tissue and performance test.
3, according to the preparation method of claim 1,2 described oriented growth column crystals or monocrystalline titanium alloy, it is characterized in that: the high energy beam current thermal source can be laser beam, electron beam, beam-plasma, electric arc, the tungsten argon arc of high-energy-density.
4, according to the preparation method of claim 1,2 described oriented growth column crystals or monocrystalline titanium alloy, it is characterized in that: promote (substrate is motionless) continuously or substrate drop-down continuously (high energy beam current thermal source processing head is motionless) by high energy beam current thermal source processing head, the high energy beam current thermal source is deposited on the titanium alloy powder continuous melting of synchronous transport on the common alloy of titanium substrate, can prepare the oriented growth cylindrulite titanium alloy ingot of random length.
5, according to the preparation method of claim 1,2 described oriented growth column crystals or monocrystalline titanium alloy, it is characterized in that: the high energy beam current thermal source is along part C AD model cross sectional slice track scanning, with the titanium alloy powder of synchronous transport successively melt deposition on the common alloy of titanium substrate, can prepare the titanium alloy component of arbitrary shape size with oriented growth columnar structure.
6, according to the preparation method of claim 1,2 described oriented growth column crystals or monocrystalline titanium alloy, it is characterized in that: select monocrystalline titanium alloy seed crystal for use, the titanium alloy powder continuous melting thereon deposition with synchronous transport can prepare monocrystalline titanium alloy ingot.
7, according to the preparation method of claim 1,2 described oriented growth column crystals or monocrystalline titanium alloy, it is characterized in that: select for use the monocrystalline titanium alloy as substrate, with the titanium alloy powder of synchronous transport melt deposition successively thereon, can prepare titanium alloy component with single crystal organization.
8, according to the preparation method of claim 1,2 described oriented growth column crystals or monocrystalline titanium alloy, it is characterized in that: the cross-sectional shape of oriented growth cylindrulite that this method prepares and monocrystalline titanium alloy ingot can be circle, ellipse, rectangle, annular.
9, according to the preparation method of claim 1,2 described oriented growth column crystals or monocrystalline titanium alloy, it is characterized in that: the high energy beam current power in the thermal source parameter is 2～500kW, high energy beam a fluid stream shape of spot is circle, ellipse, line spot and rectangle spot, and beam spot size is 1～100mm.
10, according to the preparation method of claim 1,2 described oriented growth column crystals or monocrystalline titanium alloy, it is characterized in that: it can be 2～800g/min that powder feeder is carried the powder feeding rate of titanium alloy powder stream.
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| CN103668461A (en) * | 2013-09-21 | 2014-03-26 | 北京工业大学 | Method for preparing nickel-based superalloy Rene80 directionally-grown column crystal/single crystal alloy and manufacturing parts |
| CN103862042A (en) * | 2014-02-21 | 2014-06-18 | 西安交通大学 | Method for orientated growth of superfine columnar crystal by adopting laser direct forming technology |
| CN105705278A (en) * | 2013-11-14 | 2016-06-22 | 通用电气公司 | Layered manufacturing of single crystal alloy components |
| CN106956000A (en) * | 2017-03-09 | 2017-07-18 | 南京理工大学 | A kind of fast preparation method of TiAl-base alloy drip molding |
| CN110695358A (en) * | 2019-11-11 | 2020-01-17 | 北京理工大学 | Wire material additive manufacturing method of titanium alloy single crystal blade |
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2003
- 2003-11-10 CN CN 200310113420 patent/CN1239759C/en not_active Expired - Fee Related
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN103668461A (en) * | 2013-09-21 | 2014-03-26 | 北京工业大学 | Method for preparing nickel-based superalloy Rene80 directionally-grown column crystal/single crystal alloy and manufacturing parts |
| US10569362B2 (en) | 2013-11-14 | 2020-02-25 | General Electric Company | Layered manufacturing of single crystal alloy components |
| CN105705278A (en) * | 2013-11-14 | 2016-06-22 | 通用电气公司 | Layered manufacturing of single crystal alloy components |
| US11446766B2 (en) | 2013-11-14 | 2022-09-20 | General Electric Company | Layered manufacturing of single crystal alloy components |
| CN103862042B (en) * | 2014-02-21 | 2016-04-27 | 西安交通大学 | The method of the ultra-fine column crystal oriented growth of a kind of Laser Direct Deposition |
| CN103862042A (en) * | 2014-02-21 | 2014-06-18 | 西安交通大学 | Method for orientated growth of superfine columnar crystal by adopting laser direct forming technology |
| CN106956000A (en) * | 2017-03-09 | 2017-07-18 | 南京理工大学 | A kind of fast preparation method of TiAl-base alloy drip molding |
| CN110695358A (en) * | 2019-11-11 | 2020-01-17 | 北京理工大学 | Wire material additive manufacturing method of titanium alloy single crystal blade |
| CN113182530A (en) * | 2021-05-07 | 2021-07-30 | 上海理工大学 | Additive manufacturing method of magnesium alloy directional solidified crystal or single crystal |
| CN113245562A (en) * | 2021-06-22 | 2021-08-13 | 北京煜鼎增材制造研究院有限公司 | Equipment for preparing metal test piece and structural part by high-energy beam |
| CN113245562B (en) * | 2021-06-22 | 2021-10-01 | 北京煜鼎增材制造研究院有限公司 | Equipment for preparing metal test piece and structural part by high-energy beam |
| CN113634900A (en) * | 2021-07-21 | 2021-11-12 | 上海理工大学 | Method for preparing nickel-based alloy directional twins by using additive manufacturing technology |
| 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 |
| CN114505496A (en) * | 2022-02-11 | 2022-05-17 | 北京航空航天大学 | Method for controlling oriented growth of alloy crystal grains in laser additive manufacturing process |
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