CN109628772A - A kind of super short period high intensity-high ductibility nickel aluminum bronze and preparation method - Google Patents
A kind of super short period high intensity-high ductibility nickel aluminum bronze and preparation method Download PDFInfo
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- CN109628772A CN109628772A CN201811592724.4A CN201811592724A CN109628772A CN 109628772 A CN109628772 A CN 109628772A CN 201811592724 A CN201811592724 A CN 201811592724A CN 109628772 A CN109628772 A CN 109628772A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/20—Direct sintering or melting
- B22F10/28—Powder bed fusion, e.g. selective laser melting [SLM] or electron beam melting [EBM]
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/30—Process control
- B22F10/36—Process control of energy beam parameters
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/30—Process control
- B22F10/36—Process control of energy beam parameters
- B22F10/366—Scanning parameters, e.g. hatch distance or scanning strategy
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
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- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y10/00—Processes of additive manufacturing
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C9/00—Alloys based on copper
- C22C9/01—Alloys based on copper with aluminium as the next major constituent
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- 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
- B22F12/10—Auxiliary heating means
- B22F12/17—Auxiliary heating means to heat the build chamber or platform
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
Abstract
The invention discloses a kind of preparation methods of super short period high intensity-high ductibility nickel aluminum bronze, which comprises the steps of: each powder S1, is matched by the molar ratio of Cu:Al:Ni:Fe:Mn, the average grain diameter of powder is 20-60 μm；Each powder is mixed, ingredient is obtained；S2, forging smelting by above-mentioned food ingredient and heat treatment process obtain the nickel-aluminum bronze bar that diameter is 50-100mm；S3, atomization process is carried out to above-mentioned nickel-aluminum bronze bar using plasma electrode atomization；S4, the nickel aluminum bronze powder after above-mentioned plasma electrode atomization process is obtained high density through 3D printing and is had both the high-intensitive nickel aluminum bronze with high ductibility using selective electronic beam smelting process.Precipitated phase is tiny inside alloy obtained by preparation method of the invention and is in even dispersion distribution, and alloy consistency is high, has both high-intensitive and high ductibility, and technological parameter is easy to control in preparation process, and the process-cycle is short.
Description
Technical field
The invention belongs to nickel aluminum bronze fields, and in particular to a kind of super short period high intensity-high ductibility nickel aluminium is green
The preparation method of copper alloy and obtained super short period high intensity-high ductibility nickel aluminum bronze.
Background technique
For a long time, people are dedicated to exploring the metal for being provided simultaneously with high-intensitive and high ductibility and alloy to meet need
It asks.And traditional method usually reduces its ductility while increasing the strength of materials.In recent years, some novelties is micro-
Structure design is seen, is included in materials microstructure and introduces high density dislocation (referring to document 1.He, B.B.et al.High
dislocation density-induced large ductility in deformed and partitioned
steels.Science 357,1029(2017)；Document 2.Lu, L., Shen, Y., Chen, X., Qian, L.&Lu,
K.Ultrahigh Strength and High Electrical Conductivity in Copper.Science 304,
422 (2004)), gradient nano crystal structure is (referring to document 3.Fang, T.H., Li, W.L., Tao, N.R.&Lu, K.Revealing
Extraordinary Intrinsic Tensile Plasticity in Gradient Nano-Grained
Copper.Science 331,1587-1590 (2011)) and bimodal crystal grain (referring to document 4.Wang, Y., Chen, M., Zhou,
F.&Ma,E.High tensile ductility in a nanostructured metal.Nature 419,912
It (2002)), can be efficiently against above-mentioned problem.But the more difficult Machinery Ministry for being suitable for processing complex geometric shapes of these methods
Part, simultaneously as the above method needs thus to generate caused by increasing because of control variable by multiple working process process
Machining reproducibility problem is unfavorable for manufacturing the institutional framework of mechanical part and the stability of performance.In recent years, increasing material manufacturing method
Become the ideal scheme for solving above-mentioned challenge (referring to document 5.Zheng, X.et because assigning the high-freedom degree of design and processing
al.Multiscale metallic metamaterials.Nature Mater.15,1100(2016)；Document 6.Mchugh,
K.J.et al.Fabrication of fillable microparticles and other complex 3D
microstructures.Science 357,1138(2017)).Existing research shows using laser powder melting (L-PBF)
The 316L stainless steel of technology manufacture has high-yield strength and high ductibility (referring to document 7.Wang, Y.M.et simultaneously
al.Additively manufactured hierarchical stainless steels with high strength
and ductility.Nature Mater.17,63-71(2018)；Document 8.Sun, Z., Tan, X., Tor, S.B.&Chua,
C.K.Simultaneously enhanced strength and ductility for 3D-printed stainless
steel 316L by selective laser melting.Npg Asia Mater.10(2018)；Document 9.Liu, L.et
al.Dislocation network in additive manufactured steel breaks strength-
ductility trade-off.Mater.Today 21,354-361(2018)).But current 3D printing technique is often confined to
The metal material easily welded is manufactured, such as stainless steel, titanium alloy, nickel alloy are (referring to document 10.Martin, J.H.et al.3D
Printing of high-strength aluminium alloys.Nature 549,365-369 (2017)), it is beaten using 3D
Print technology manufactures the copper alloy of institutional framework densification, function admirable, is at present still a problem.For example use L-PBF technology
There is partial melting phenomenon during manufacture copper alloy, cause its relative density less than 95% (referring to document 11.Zhang,
D.Q.,Liu,Z.H.&Chua,C.K.Investigation on forming process of copper alloys via
Selective Laser Melting.In High Value Manufacturing:Advanced Research in
Virtual and Rapid Prototyping:Proceedings of the 6th International Conference
on Advanced Research in Virtual and Rapid Prototyping,Leiria,Portugal 285
(2013)).By regulating and controlling 3D printing machined parameters, obtained Cu-Cr-Zr-Ti alloy relative density reaches 97.9%, but due to
The internal grain size of drip molding is mainly 30-250 μm of column crystal, therefore its tensile strength (UTS) is than traditional forging and molding
The low 20-25% of part is (referring to document 12.Popovich, A.et al.Microstructure and mechanical
properties of additive manufactured copper alloy.Mater.Lett.179,38-41(2016))。
Selective electronic beam melting (SEBM) is one of the key technology of metal 3D printing manufacture, using electron beam in height
Metal powder is subjected to selective sintering to manufacture components under vacuum.Compared with selective laser melts (SLM), SEBM technology
Heating environment and higher energy density more evenly can be provided in 3D printing copper alloy, overcome copper alloy to SLM
The low problem of S. E. A. in technology.Meanwhile it (rushing base-anneal-to strike out compared with conventional method manufactures copper alloy component
Shape-annealing-passivation, it is sometimes desirable to which Multi-step forming processing is annealed repeatedly), SEBM technology can the conjunction of disposal molding nickel-aluminum bronze
Golden component, and density is close completely fine and close, relative density is greater than 99%, mechanical property (including tensile strength and stretching elongation)
Better than the similar product of forging technology manufacture, have the advantages that the process-cycle is short, high-efficient.
Summary of the invention
For at least one of prior art the above defects or improvement requirements, it is high that the present invention provides a kind of super short periods
Intensity-high ductibility nickel aluminum bronze preparation method, gained alloy inside precipitated phase is tiny and is distributed shape in even dispersion
State, alloy consistency is high, has both high-intensitive and high ductibility, and technological parameter is easy to control in preparation process, and the process-cycle is short.
To achieve the above object, according to one aspect of the present invention, a kind of super short period high intensity-high ductibility is provided
The preparation method of nickel aluminum bronze, which comprises the steps of:
S1, molar ratio=(residue) by Cu:Al:Ni:Fe:Mn: (8-12): (3.5-6.5): (2.5-5.5): (0.8-
1.2) Cu powder, Al powder, Ni powder, Fe powder and Mn powder, are chosen, the average grain diameter of powder is 20-60 μm；By Cu powder, Al powder, Ni powder,
Fe powder and the mixing of Mn powder, obtain ingredient；
S2, forging smelting by above-mentioned food ingredient and heat treatment process obtain the nickel-aluminum bronze that diameter is 50-100mm
Bar；
S3, atomization process is carried out to above-mentioned nickel-aluminum bronze bar using plasma electrode atomization；
S4, by the nickel aluminum bronze powder after above-mentioned plasma electrode atomization process, melted using selective electronic beam
Technique obtains high density through 3D printing and has both the high-intensitive nickel aluminum bronze with high ductibility.
Preferably, in step S1, molar ratio=81.1:9.5:4.2:4.0:1.2 of Cu:Al:Ni:Fe:Mn.
Preferably, the fusion process in step S2 carries out in high-purity argon gas or nitrogen environment.
Preferably, the plasma electrode atomization process in step S3 carries out in high-purity argon gas or nitrogen environment.
Preferably, in step s3, the process conditions of the plasma electrode atomization process are as follows: electrode bar revolving speed is
15000-30000r/min, electrode bar diameter are 50-100mm.
Preferably, in step s 4, the selective electronic beam smelting process condition are as follows:
3D printing bottom plate preheating temperature is 400-800 DEG C, and 3D printing scanning speed is 20-50m/s；Print scanned speed is
0.5-1m/s, Single Slice Mode use reciprocating manner, and it is 0-90 ° that interlayer, which rotates angle, fills spacing 0.15mm, scanning electron line
2-5mA, plasma electrode are atomized 45-105 μm of spherical powder diameter range.
To achieve the above object, according to one aspect of the present invention, a kind of foregoing preparation method of application is also provided
High intensity obtained-high ductibility nickel aluminum bronze, nickel aluminum bronze tensile strength 900MPa or more, preferably
960Mpa or more, Uniform Tension rate elongation is 30% or more, and relative density is 99% or more.
Above-mentioned preferred feature can be combined with each other as long as they do not conflict with each other.
In general, through the invention it is contemplated above technical scheme is compared with the prior art, have below beneficial to effect
Fruit:
1, super short period of the invention high intensity-high ductibility nickel aluminum bronze preparation method, the nickel being prepared
The distribution of aluminium bronze precipitated phase even dispersion overcomes conventional preparation techniques and causes precipitated phase dispersion uneven and lead to mechanical property
The deficiency that can decline；
2, super short period of the invention high intensity-high ductibility nickel aluminum bronze preparation method, the nickel being prepared
Aluminium bronze consistency is high, good mechanical performance.
3, super short period of the invention high intensity-high ductibility nickel aluminum bronze preparation method, preparation process is simple,
Quick, the inexpensive preparation that labyrinth workpiece can be achieved can theoretically prepare and appoint in 3D printing equipment size allowed band
The nickel-aluminum bronze components of meaning labyrinth.
4, super short period of the invention high intensity-high ductibility nickel aluminum bronze preparation method, using selective electricity
Metal powder is carried out selective sintering under a high vacuum using electron beam to manufacture zero by beamlet smelting process (SEBM)
Part.Compared with selective laser melts (SLM), SEBM technology can provide heating ring more evenly in 3D printing copper alloy
Border and higher energy density overcome the copper alloy problem low to S. E. A. in SLM technology.Meanwhile with tradition side
Legal system make copper alloy component compared to (rush base-annealing-it is stamping-annealing-passivation, it is sometimes desirable to it is Multi-step forming processing, anti-
Retire from active military service fire), SEBM technology can disposal molding nickel aluminum bronze component, and density, close to completely fine and close, relative density is greater than
99%, mechanical property (including tensile strength and stretching elongation) has processing week better than the similar product of forging technology manufacture
Phase short, high-efficient advantage.
Detailed description of the invention
Fig. 1 is the process flow of super short period high intensity-high ductibility nickel aluminum bronze preparation method of the invention
Schematic diagram；
Fig. 2 is the embodiment of super short period high intensity-high ductibility nickel aluminum bronze preparation method of the invention
Schematic diagram；
Fig. 3 is in super short period high intensity-high ductibility nickel aluminum bronze preparation method of the invention, using etc. from
The scanning electron microscope (SEM) photograph of the nickel aluminum bronze powder of sub-electrode atomization preparation；
Fig. 4 is in super short period high intensity-high ductibility nickel aluminum bronze preparation method of the invention, using etc. from
The grain size distribution schematic diagram of the nickel aluminum bronze powder of sub-electrode atomization preparation；
Fig. 5 is the high intensity of super short period made from the embodiment of the present invention 1-high ductibility nickel aluminum bronze polishing etch
Surface sweeping electromicroscopic photograph afterwards；
Fig. 6 is that the stretching of the high intensity of super short period made from the embodiment of the present invention 1-high ductibility nickel aluminum bronze is surveyed
Test result；
Fig. 7 is that the stretching of the high intensity of super short period made from the embodiment of the present invention 2-high ductibility nickel aluminum bronze is surveyed
Test result；
Fig. 8 is that the stretching of the high intensity of super short period made from the embodiment of the present invention 3-high ductibility nickel aluminum bronze is surveyed
Test result；
Fig. 9 is that the high intensity of super short period made from the embodiment of the present invention 1-3-high ductibility nickel aluminum bronze is opposite
Density measurement result.
Specific embodiment
In order to make the objectives, technical solutions, and advantages of the present invention clearer, with reference to the accompanying drawings and embodiments, right
The present invention is further elaborated.It should be appreciated that the specific embodiments described herein are merely illustrative of the present invention, and
It is not used in the restriction present invention.As long as in addition, technical characteristic involved in the various embodiments of the present invention described below
Not constituting a conflict with each other can be combined with each other.The present invention is described in more detail With reference to embodiment.
Embodiment 1:
As shown in Figs. 1-2, the preparation side of a kind of super short period high intensity-high ductibility nickel aluminum bronze of the invention
Method includes the following steps:
1) press Cu:Al:Ni:Fe:Mn molar ratio=81.1:9.5:4.2:4.0:1.2, choose Cu powder, Al powder, Ni powder,
Fe powder and Mn powder, the average grain diameter of powder are 45 μm；Cu powder, Al powder, Ni powder, Fe powder and Mn powder are uniformly mixed, obtained initial
Ingredient；
2) smelting by above-mentioned food ingredient, forging and heat treatment process obtain the nickel-aluminum bronze bar that diameter is 76mm,
Fusion process carries out in high-purity argon gas atmosphere；
3) atomization process is carried out to above-mentioned nickel-aluminum bronze bar using plasma electrode atomization, be atomized in high-purity argon gas
It carries out, plasma electrode atomization process are as follows: electrode bar revolving speed is 20000r/min, and electrode bar diameter is 76mm, obtains particle ruler
Very little is 45-105 μm of spherical powder；
4) to the nickel aluminum bronze powder of above-mentioned plasma electrode atomization preparation, work is melted using selective electronic beam
Skill obtains high density through 3D printing and has both the high-intensitive nickel aluminum bronze with high ductibility.Wherein selective electronic beam
Smelting process are as follows: printing bottom plate preheating temperature is 600 DEG C, and 3D printing scanning speed is 50m/s；Print scanned speed is 1m/s,
Single Slice Mode uses reciprocating manner, and it is 90 ° that interlayer, which rotates angle, fills spacing 0.15mm, scanning electron line 5mA, plasma
Electrode atomized 45-105 μm of spherical powder diameter range.
Fig. 3 is the scanning electricity of the nickel aluminum bronze powder in the present invention using the preparation of plasma rotating electrode atomization method
Mirror figure, Fig. 4 are that the grain size distribution of the nickel aluminum bronze powder in the present invention using the preparation of plasma electrode atomization is shown
It is intended to, it is seen then that powder sphericity is preferable, and spherical powder size is distributed between 45-105 μm.
Fig. 5 is the high intensity of super short period made from the embodiment of the present invention 1-high ductibility nickel aluminum bronze polishing etch
Surface sweeping electromicroscopic photograph afterwards, it is seen then that prepared nickel-aluminum bronze precipitated phase is evenly distributed, and can improve its mechanical property.
Fig. 6 is that the stretching of the high intensity of super short period made from the embodiment of the present invention 1-high ductibility nickel aluminum bronze is surveyed
Test result, it is seen that its tensile strength reaches 996MPa, and with existing literature data comparison, tensile strength is greatly improved.
Embodiment 2:
1) press Cu:Al:Ni:Fe:Mn molar ratio=81.1:9.5:4.2:4.0:1.2, choose Cu powder, Al powder, Ni powder,
Fe powder and Mn powder, the average grain diameter of powder are 45 μm；Cu powder, Al powder, Ni powder, Fe powder and Mn powder are uniformly mixed, obtained initial
Ingredient；
2) smelting by above-mentioned food ingredient, forging and heat treatment process obtain the nickel-aluminum bronze bar that diameter is 76mm,
Fusion process carries out in high-purity argon gas atmosphere；
3) atomization process is carried out to above-mentioned nickel-aluminum bronze bar using plasma electrode atomization, be atomized in high-purity argon gas
It carries out, plasma electrode atomization process are as follows: electrode bar revolving speed is 20000r/min, and electrode bar diameter is 76mm, obtains particle ruler
Very little is 45-105 μm of spherical powder；
4) to the nickel aluminum bronze powder of above-mentioned plasma electrode atomization preparation, work is melted using selective electronic beam
Skill obtains high density through 3D printing and has both the high-intensitive nickel aluminum bronze with high ductibility.Wherein selective electronic beam
Smelting process are as follows: printing bottom plate preheating temperature is 600 DEG C, and 3D printing scanning speed is 50m/s；Print scanned speed is 1m/s,
Single Slice Mode uses reciprocating manner, and it is 90 ° that interlayer, which rotates angle, fills spacing 0.15mm, scanning electron line 5mA, plasma
Electrode atomized 63-75 μm of spherical powder diameter range.
Fig. 7 is that the high intensity of super short period made from the embodiment of the present invention 2-high ductibility nickel aluminum bronze tension is surveyed
Test result, tensile strength reach 1035MPa, and the more traditional forging nickel-aluminum bronze of mechanical property is greatly improved.High
Caused by the nickel-aluminum bronze crystal grain that yield strength is mainly prepared due to SEBM is tiny, and precipitated phase is evenly distributed.
Embodiment 3:
1) press Cu:Al:Ni:Fe:Mn molar ratio=81.1:9.5:4.2:4.0:1.2, choose Cu powder, Al powder, Ni powder,
Fe powder and Mn powder, the average grain diameter of powder are 45 μm；Cu powder, Al powder, Ni powder, Fe powder and Mn powder are uniformly mixed, obtained initial
Ingredient；
2) smelting by above-mentioned food ingredient, forging and heat treatment process obtain the nickel-aluminum bronze bar that diameter is 76mm,
Fusion process carries out in high-purity argon gas atmosphere；
3) atomization process is carried out to above-mentioned nickel-aluminum bronze bar using plasma electrode atomization, be atomized in high-purity argon gas
It carries out, plasma electrode atomization process are as follows: electrode bar revolving speed is 20000r/min, and electrode bar diameter is 76mm, obtains particle ruler
Very little is 45-105 μm of spherical powder；
4) to the nickel aluminum bronze powder of above-mentioned plasma electrode atomization preparation, work is melted using selective electronic beam
Skill obtains high density through 3D printing and has both the high-intensitive nickel aluminum bronze with high ductibility.Wherein selective electronic beam
Smelting process are as follows: printing bottom plate preheating temperature is 600 DEG C, and 3D printing scanning speed is 50m/s；Print scanned speed is 1m/s,
Single Slice Mode uses reciprocating manner, and it is 90 ° that interlayer, which rotates angle, fills spacing 0.15mm, scanning electron line 5mA, plasma
Electrode atomized 75-105 μm of spherical powder diameter range.
Fig. 8 is that the high intensity of super short period made from the embodiment of the present invention 3-high ductibility nickel aluminum bronze tension is surveyed
Test result, tensile strength reach 960MPa, and the more traditional forging nickel-aluminum bronze of mechanical property is greatly improved.
Fig. 9 is super short period high intensity-high ductibility nickel aluminum bronze obtained by test the embodiment of the present invention 1,2,3
Relative density as a result, the relative density for showing the nickel aluminum bronze 99% or more, show the nickel aluminum bronze have
Standby fine and close microstructure, it is ensured that it is with excellent mechanical property.
Each raw material cited by the present invention can realize that the bound value of the present invention and each raw material, interval value can
Realize the present invention, the bound value and interval value of technological parameter (such as air pressure, temperature, time, vacuum degree) of the invention
It can realize the present invention, embodiment numerous to list herein.As it will be easily appreciated by one skilled in the art that the foregoing is merely this hairs
Bright preferred embodiment, is not intended to limit the invention, done within the spirit and principles of the present invention any to repair
Change, equivalent replacement and improvement etc., should all be included in the protection scope of the present invention.
Claims (7)
1. a kind of preparation method of super short period high intensity-high ductibility nickel aluminum bronze, which is characterized in that including walking as follows
It is rapid:
S1, molar ratio=(residue) by Cu:Al:Ni:Fe:Mn: (8-12): (3.5-6.5): (2.5-5.5): (0.8-1.2),
Cu powder, Al powder, Ni powder, Fe powder and Mn powder are chosen, the average grain diameter of powder is 20-60 μm；By Cu powder, Al powder, Ni powder, Fe powder and
The mixing of Mn powder, obtains ingredient；
S2, forging smelting by above-mentioned food ingredient and heat treatment process obtain the nickel-aluminum bronze bar that diameter is 50-100mm；
S3, atomization process is carried out to above-mentioned nickel-aluminum bronze bar using plasma electrode atomization；
S4, by the nickel aluminum bronze powder after above-mentioned plasma electrode atomization process, using selective electronic beam smelting process,
High density is obtained through 3D printing and has both the high-intensitive nickel aluminum bronze with high ductibility.
2. the preparation method of super short period high intensity-high ductibility nickel aluminum bronze as described in claim 1, feature exist
In:
In step S1, molar ratio=81.1:9.5:4.2:4.0:1.2 of Cu:Al:Ni:Fe:Mn.
3. the preparation method of super short period high intensity-high ductibility nickel aluminum bronze as described in claim 1, feature exist
In:
Fusion process in step S2 carries out in high-purity argon gas or nitrogen environment.
4. the preparation method of super short period high intensity-high ductibility nickel aluminum bronze as described in claim 1, feature exist
In:
Plasma electrode atomization process in step S3 carries out in high-purity argon gas or nitrogen environment.
5. the preparation method of super short period high intensity-high ductibility nickel aluminum bronze as described in claim 1, feature exist
In:
In step s3, the process conditions of the plasma electrode atomization process are as follows: electrode bar revolving speed is 15000-30000r/
Min, electrode bar diameter are 50-100mm.
6. the preparation method of super short period high intensity-high ductibility nickel aluminum bronze as described in claim 1, feature exist
In:
In step s 4, the selective electronic beam smelting process condition are as follows:
3D printing bottom plate preheating temperature is 400-800 DEG C, and 3D printing scanning speed is 20-50m/s；Print scanned speed is 0.5-
1m/s, Single Slice Mode use reciprocating manner, and it is 0-90 ° that interlayer, which rotates angle, fills spacing 0.15mm, scanning electron line 2-
5mA, plasma electrode are atomized 45-105 μm of spherical powder diameter range.
7. high intensity-high ductibility nickel aluminum bronze made from application preparation method as claimed in any one of claims 1 to 6,
It is characterized by:
Nickel aluminum bronze tensile strength is in 900MPa or more, and 30% or more, relative density exists Uniform Tension rate elongation
99% or more.
Priority Applications (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201811592724.4A CN109628772B (en) | 2018-12-25 | 2018-12-25 | Ultrashort-period high-strength and high-ductility nickel-aluminum bronze alloy and preparation method thereof |
| PCT/CN2019/076406 WO2020133680A1 (en) | 2018-12-25 | 2019-02-28 | Super short period nickel-aluminum-bronze alloy having high-strength and high-ductility, and preparation method therefor |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201811592724.4A CN109628772B (en) | 2018-12-25 | 2018-12-25 | Ultrashort-period high-strength and high-ductility nickel-aluminum bronze alloy and preparation method thereof |
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| Publication Number | Publication Date |
|---|---|
| CN109628772A true CN109628772A (en) | 2019-04-16 |
| CN109628772B CN109628772B (en) | 2020-04-10 |
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| CN201811592724.4A Active CN109628772B (en) | 2018-12-25 | 2018-12-25 | Ultrashort-period high-strength and high-ductility nickel-aluminum bronze alloy and preparation method thereof |
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| CN110102762A (en) * | 2019-04-24 | 2019-08-09 | 北京遥感设备研究所 | A kind of Mn-Cu and Fe-Ni dissimilar material gradient-structure manufacturing process |
| CN113210813A (en) * | 2021-04-22 | 2021-08-06 | 浙江富春江水电设备有限公司 | Welding method of nickel-aluminum-bronze workpiece |
| CN114990380A (en) * | 2022-06-24 | 2022-09-02 | 上海交通大学 | Beryllium-free super high-strength high-toughness copper alloy and preparation method thereof |
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