CN109338182A - A kind of Al-Mg-Er-Zr series alloys and preparation method - Google Patents

A kind of Al-Mg-Er-Zr series alloys and preparation method Download PDF

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CN109338182A
CN109338182A CN201811354148.XA CN201811354148A CN109338182A CN 109338182 A CN109338182 A CN 109338182A CN 201811354148 A CN201811354148 A CN 201811354148A CN 109338182 A CN109338182 A CN 109338182A
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aluminium alloy
alloy
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molded part
preparation
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张志杰
耿遥祥
许俊华
喻利花
鞠洪博
李洁
樊世敏
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Jiangsu University of Science and Technology
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • 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]
    • 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
    • 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
    • B22F10/32—Process control of the atmosphere, e.g. composition or pressure in a building chamber
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
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    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B22F10/30—Process control
    • B22F10/36—Process control of energy beam parameters
    • 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
    • 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
    • B22F10/60—Treatment of workpieces or articles after build-up
    • B22F10/64—Treatment of workpieces or articles after build-up by thermal means
    • 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
    • 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
    • C22C1/026—Alloys based on aluminium
    • 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
    • C22C1/03—Making non-ferrous alloys by melting using master alloys
    • 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
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium as the next major constituent
    • 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
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Abstract

The invention discloses a kind of Al-Mg-Er-Zr series alloys and preparation methods.The alloy is by mass percentage by component: Mg 6-12%, Er 0.5-2%, Zr 0.5-2%, and surplus is Al composition.Aluminium alloy molded part is made by foundry alloy melting, metal powder preparation, the preparation of aluminium alloy molded part and heat treatment process step.The present invention uses precinct laser fusion manufacturing technology, greatly improves solubility of Mg, Er and Zr alloying element in aluminum substrate, increases solution strengthening element Mg and dispersion-strengtherning particle Al in aluminium alloy3The concentration of Er improves the mechanical property of aluminium alloy.Gained aluminium alloy highest consistency is 99%, the maximum tensile strength σbUp to 570MPa, yield strength σ0.2Up to 530MPa, and there is the rate of plastic deformation greater than 7%.Compared with the Al-Mg-Sc-Zr aluminium alloy obtained using selective laser melting process, the mechanical property for the Al-Mg-Er-Zr series alloys which obtains is suitable with it, but significantly reduces cost of material.It is applicable to the higher complex structural member of mechanical property requirements.

Description

A kind of Al-Mg-Er-Zr series alloys and preparation method
Technical field
The invention belongs to field of material technology, are related to a kind of aluminum alloy materials, specifically relate to a kind of Al-Mg-Er-Zr The preparation method of line aluminium alloy composition and its molded part.
Background technique
Deforming Al-Mg alloy is one of numerous aluminium alloys, it belongs to not heat-treatable strengthened type aluminium alloy, is had single Phase constitution.Therefore, which has good corrosion stability and solderability, is widely used in aerospace, electric, traffic fortune The fields such as defeated, bridge construction, and have broad application prospects in fields such as the energy, daily necessities, stationery sports goods.Due to Al-Mg Alloy has huge market potential, the just attention by various countries.But since the alloy deviates Al-Mg eutectic point, and belong to solid Molten reinforced aluminium alloy, forming property and strength character are relatively poor, it is difficult to carry out the forming of complex parts and obtain high-strength The constitutional detail of degree, therefore, formability and strength character become manufacture complexity, a main system of high-strength aluminum-magnesium alloy product About factor.
After a small amount of Zr, Sc, Er element is added in Al-Mg alloy, by the solid solution and ageing treatment in later period, it can be closed in aluminium Al is precipitated in coherence in matrix3Zr、Al3Sc or Al3Er particle, plays the role of second-phase strength.In addition, Sc and/or Er rare earth closes The addition of alloying element is other than playing the role of second-phase strength while can also refine crystal grain, enhances the mechanical property of aluminium alloy Energy.The better effect when these elements compoundings are added.The microelements such as compound addition Sc, Zr can not only be shown in Al-Mg alloy The as-cast structure for improving alloy is write, and the recrystallization temperature of Al-Mg alloy can be significantly improved, the reinforcing of substructure is promoted to imitate Fruit, so that the comprehensive performance of alloy is dramatically improved on the original basis, Al-Mg-Sc-Zr alloy strength height, plasticity and toughness It is good, anti-corrosion and welding performance is excellent, before the high-new sharp technical field application such as ship, aerospace industry, rocket-powered missile, nuclear energy Scape is very wide.However Sc is expensive, keeps Al-Mg-Sc-Zr Alloyapplication limited.The Al-Er alloy of identical mass fraction Price be about Al-Sc alloy price 1/30, Er substitution Sc after the cost of aluminium alloy, therefore Al-Mg-Er-Zr can be greatly reduced The development of alloy is significant.Meanwhile in conventional casting techniques, solid solubility of the Er and Zr element in Al element is minimum, makes After obtaining postmenstruation solid solution and ageing treatment, secondary Al3Amount of precipitation of (Er, the Zr) enhanced particles in aluminium alloy is limited, while Mg Solid solution capacity in aluminium alloy is also limited, and cannot achieve continuing to increase for Al-Mg-Er-Zr line aluminium alloy intensity.
The one kind of selective laser melting process as rapid shaping technique, the basic principle is that according to the CAD model of part Slicing delamination processing is carried out, is scanned using digital control system control workbench according to the path that delamination software is set, by swashing Light fusing metal powder, which is layering, obtains near-purification formation of parts.Since small with laser spot diameter, scanning speed is fast, constituency is swashed Light smelting technology has many advantages, such as that production procedure is short, part has excellent performance and can realize accurate complex structural member disposal molding, Breakthrough development will be brought for manufacturing industry.
Selective laser melting (SLM) molding process, which is divided into, to be rapidly heated and two stages of rapid cooling: laser and metal-powder first Interaction, since metal powder absorbs the energy of laser, temperature rises suddenly and has been more than the fusing point formation molten bath of metal, this When, molten metal is in liquid equilibrium, and metallic atom can move freely, and alloying element is uniformly distributed；After laser is removed, by In the disappearance of heat source, bath temperature is with 103-106The speed of K/s declines.In the process, the expansion of metallic atom and alloying element It dissipates mobile restricted, it is suppressed that the segregation of crystal grain grown up with alloying element, the metal structure crystal grain after solidification is tiny, alloying element It is evenly distributed, the plasticity of aluminium alloy can be greatly improved.Meanwhile alloy element in alloy can be effectively increased using this technology Solid solubility.For Al-Mg-Er-Zr line aluminium alloy, then can be passed through based on the characteristic of selective laser melting process melt supercooled Increase the content of Mg, Er and Zr element in alloy, realize the promotion of Mg, Er and Zr solid solubility in aluminum substrate, and then passes through the later period Ageing treatment, obtain more Al3(Er, Zr) enhanced particles realize further mentioning for Al-Mg-Er-Zr line aluminium alloy intensity It rises.However, the al alloy component of selective laser melting process application now can not embody still based on conventional cast alloying component The operational characteristic of the melt supercooled of selective laser melting process is designed by ingredient and realizes Al-Mg-Er-Zr line aluminium alloy performance Further promotion.
Summary of the invention
The purpose of the present invention is: the 1. disadvantage with high costs for Al-Mg-Sc-Zr alloy raw material, after substituting Sc by Er Alloy raw material cost can be greatly reduced；2. Mg, Er and Zr solid solution in the Al-Mg-Er-Zr alloy obtained for conventional casting techniques Element additive amount is limited, cannot achieve the shortcomings that Al-Mg-Er-Zr alloy mechanical property is further promoted, can pass through precinct laser Solid solubility of Mg, Er and Zr element in Al is substantially improved in smelting technology, to realize Al-Mg-Er-Zr alloy mechanical property Effectively promoted.
In order to achieve the above objectives, The technical solution adopted by the invention is as follows:
A kind of Al-Mg-Er-Zr line aluminium alloy, by mass percentage by ingredient and content: Mg 6-12%, Er 0.5- 2%, Zr 0.5-2%, surplus are Al composition, and gross mass percentage is 100%.
Further preferably, the fine aluminium that the purity of the aluminium (Al) is >=99.9%.
Further preferably, the pure magnesium that the purity of the magnesium (Mg) is >=99.5%.
Further preferably, the erbium (Er) is by mass percentage for Al90Er10Or Al80Er20Intermediate alloy form is added.
Further preferably, the zirconium (Zr) is by mass percentage for Al90Zr10Intermediate alloy form is added.
In order to achieve the above objectives, another technical solution that the present invention uses is as follows:
A kind of preparation method of Al-Mg-Er-Zr line aluminium alloy, includes the following steps:
S1: foundry alloy melting: after crucible is preheated to 500 ± 8 DEG C, by mass percentage, fine aluminium is first placed in crucible In, 1200 ± 8 DEG C are continuously heating to, after fine aluminium fusing, then by Al90Zr10Intermediate alloy is added in fine aluminium, stirs 50 minutes, It is to be mixed uniformly after, melt temperature is down to 900 ± 5 DEG C, Mg simple substance and Al is then added80Er20Intermediate alloy stirs 50 points Clock obtains ingredient uniform alloy melt；
S2: powder preparation: opening crucible bottom valve, and alloy melt is flowed out through the oxidation aluminum tubular conductor that internal diameter is 10mm, from By falling, liquid stream, at fine drop, forms metal powder after solidification through high pressure nitrogen atomizer impact grinding；
S3: the preparation of aluminium alloy molded part:
1) threedimensional model of forming parts needed for being established using CAD, and convert thereof into the data format that can be cut；
2) SLM device is imported after threedimensional model being cut into the multilayer with a thickness of 0.05mm together with supporter；
3) high pure nitrogen is poured into SLM device cabinet, is tested when oxygen content in cabinet is less than 200ppm；
4) in one layer of removable substrate upper berth 0.05mm metal powder as described in step S2；
5) geometry of laser scanning step 4) metal powder layer cross section 2 times, laser facula in scanning process are as follows: 0.1mm, the spacing in twice sweep path are as follows: 0.1mm, laser power are as follows: 200-300W, laser scan rate are as follows: 500- 1500mm/s；
6) substrate is declined into the thickness that a layer is 0.05mm, in the new metal powder in one layer of substrate upper berth；Laser scanning Geometry 1 time of new paving metal powder layer cross section, laser facula in scanning process are as follows: 0.1mm, between twice sweep path Away from are as follows: 0.1mm, laser power are as follows: 200-300W, laser scan rate are as follows: 500-1500mm/s, scanning direction are swept with upper one layer It retouches direction and rotates clockwise 45 degree；
7) step 6) is repeated repeatedly, number of repetition is molded part height ÷ powdering thickness -2, after the end of the program, is obtained The aluminium alloy molded part；
S4: heat treatment:
2-12h is heat-treated under the conditions of aluminium alloy molded part obtained in step S3 is placed in 150-300 DEG C to get Al- is arrived Mg-Er-Zr line aluminium alloy molded part.
Further preferably, the diameter of metal powder described in step S2 is 20~50 microns.
Further preferably, the purity of high pure nitrogen described in step S3 is 99.999%.
Further preferably, the pressure of atomization described in step S2 is 20MPa.
The advantages of the present invention are:
(1) operational characteristic that the present invention relies on selective laser melting process melt cooling rate high, by Al-Mg-Er-Zr The content of Er, Zr and Mg element is greatly improved in line aluminium alloy, so that alloy during Post isothermal treatment, does not need at solid solution Reason directly just can have more Al by ageing treatment3(Er, Zr) enhanced particles are precipitated, thus by increasing Al3(Er,Zr) The content of disperse educt particle and Mg solid solution element realizes effective promotion of Al-Mg line aluminium alloy comprehensive performance；
(2) present invention is by the Sc element in Er replacement Al-Mg-Sc-Zr alloy, can be greatly reduced the raw material of alloy at This, expands the application field of such material.
(3) precinct laser fusion is carried out using dedicated Al-Mg-Er-Zr line aluminium alloy powder of the invention prepare molded part, Its consistency is higher than 99%, and obtained molded part comprehensive mechanical property is substantially better than traditional Al-Mg-Sc-Zr and Al-Mg-Er-Zr It is cast aluminium alloy gold, it is suitable with the Al-Mg-Sc-Zr line aluminium alloy that existing selective laser melting process obtains.It is logical using the present invention Cross the maximum tensile strength σ of the Al-Mg-Er-Zr line aluminium alloy tensioning member of selective laser melting process acquisitionbReachable 530MPa, Yield strength σ0.2 up to 570MPa, and the maximum extension rate of alloy is up to 15%.
Specific embodiment
In order to make the objectives, technical solutions, and advantages of the present invention clearer, it is exemplified below embodiment, to the present invention It is described in further detail.It should be appreciated that described herein, the specific embodiments are only for explaining the present invention, is not used to Limit the present invention.
Embodiment 1:
One, the ingredient and content of aluminum alloy composition:
Al93Mg6Er0.5Zr0.5, wherein the purity of Al is >=99.9%；The purity of Mg is >=99.5%；Er presses quality hundred Divide than for Al90Er10Or Al80Er20Intermediate alloy form is added；Zr is with Al by mass percentage90Zr10Intermediate alloy form It is added.
Two, the preparation step of aluminium alloy molded part:
(1) foundry alloy melting:
After crucible is preheated to 500 ± 8 DEG C, fine aluminium is placed in crucible, 1200 ± 8 DEG C are continuously heating to, to fine aluminium By Al after fusing90Zr10(mass percent) intermediate alloy is pressed into fine aluminium, and is stirred 50 minutes, it is to be mixed uniformly after, Melt temperature is down to 900 ± 5 DEG C, Mg simple substance and Al is then added90Er10Or Al80Er20(mass percent) alloy, and carry out Stirring 50 minutes obtains ingredient uniform alloy melt；
(2) prepared by powder:
After alloy melt fusing uniformly, crucible bottom valve, the oxidation aluminum tubular conductor that alloy melt is 10mm through internal diameter are opened Outflow, free-falling, liquid stream, at fine drop, form metal powder after solidification through high pressure nitrogen atomizer impact grinding；Atomization Pressure is 20MPa, and it is spare to finally screen 15-60 microns of powder；
(3) preparation of aluminium alloy molded part:
1) threedimensional model of forming parts needed for being established using CAD, and convert thereof into the data format that can be cut；
2) SLM device is imported after threedimensional model being cut into the multilayer with a thickness of 0.05mm together with supporter；
3) high-purity flowing nitrogen is poured into SLM device cabinet, can be carried out when oxygen content in cavity is less than 200ppm Experiment；
4) in one layer of removable substrate upper berth 0.05mm metal powder as described in step S2；
5) geometry of laser scanning step 3) metal powder layer cross section 2 times, laser facula in scanning process are as follows: 0.1mm, the spacing in twice sweep path are as follows: 0.1mm, laser power are as follows: 200W, laser scan rate are as follows: 1000mm/s；
6) substrate declines the thickness of a layer 0.05mm, in the new metal powder in one layer of basal plane upper berth；Laser scanning is newly spread The geometry of metal powder layer cross section 1 time, laser facula are as follows: 0.1mm, the spacing in twice sweep path are as follows: 0.1mm swashs Optical power are as follows: 200W, laser scan rate are as follows: 1000mm/s；Scanning direction and upper one layer of scanning direction rotate clockwise 45 Degree；
7) step 6) is repeated repeatedly, number of repetition is molded part height ÷ powdering thickness -2, after the end of the program, is obtained The aluminium alloy molded part；
(4) it is heat-treated:
Aluminium alloy molded part obtained in step 7) is placed under the conditions of 300 DEG C and is heat-treated 1h, high-performance can be obtained Al93Mg6Er0.5Zr0.5Aluminium alloy molded part.
Three, the Mechanics Performance Testing and beneficial effect of the present embodiment
1, Mechanics Performance Testing:
Structure inspection is carried out to obtained aluminum alloy sample using X-ray diffractometer (XRD) and transmission electron microscope (TEM) It surveys；Utilize the microstructure of metallographic microscope (OM) scanning electron microscope (SEM) observation aluminum alloy sample；Using omnipotent mechanics The intensity of testing machine test aluminum alloy sample.
2, the utility model has the advantages that
1) it is higher than 99.5% by the consistency that this embodiment obtains molded part；
2) the yield strength σ of the standard tensile style obtained by this embodiment0.2For 430MPa, tensile strength sigmabFor 506MPa, the rate of plastic deformation 15%.
Embodiment 2:
One, the ingredient and content of aluminum alloy composition:
Al88Mg10Er1Zr1, wherein the purity of Al is >=99.9%；The purity of Mg is >=99.5%；Er is by mass percentage For with Al90Er10Or Al80Er20Intermediate alloy form is added；Zr is with Al by mass percentage90Zr10Intermediate alloy form adds Enter.
Two, the preparation step of aluminium alloy molded part:
(1) foundry alloy melting:
With step (1) in embodiment 1.
(2) prepared by powder:
With step (2) in embodiment 1.
(3) preparation of aluminium alloy molded part:
1) threedimensional model of forming parts needed for being established using CAD, and convert thereof into the data format that can be cut；
2) SLM device is imported after threedimensional model being cut into the multilayer with a thickness of 0.05mm together with supporter；
3) high-purity flowing nitrogen is poured into SLM device cabinet, can be carried out when oxygen content in cavity is less than 200ppm Experiment；
4) in one layer of removable substrate upper berth 0.05mm metal powder as described in step S2；
5) geometry of laser scanning step 3) metal powder layer cross section 2 times, laser facula in scanning process are as follows: 0.1mm, the spacing in twice sweep path are as follows: 0.1mm, laser power are as follows: 250W, laser scan rate are as follows: 900mm/s；
6) substrate declines the thickness of a layer 0.05mm, in the new metal powder in one layer of basal plane upper berth；Laser scanning is newly spread The geometry of metal powder layer cross section 1 time, laser facula are as follows: 0.1mm, the spacing in twice sweep path are as follows: 0.1mm swashs Optical power are as follows: 250W, laser scan rate are as follows: 900mm/s；Scanning direction and upper one layer of scanning direction rotate clockwise 45 degree；
7) step 6) is repeated repeatedly, number of repetition is molded part height ÷ powdering thickness -2, after the end of the program, is obtained The aluminium alloy molded part；
(4) it is heat-treated:
Aluminium alloy molded part obtained in step 7) is placed under the conditions of 350 DEG C and is heat-treated 1h, high-performance can be obtained Al88Mg10Er1Zr1Aluminium alloy molded part.
Three, the Mechanics Performance Testing and beneficial effect of the present embodiment
1, Mechanics Performance Testing:
With embodiment 1.
2, the utility model has the advantages that
It 1) is 99.1% by the consistency that this embodiment obtains molded part；
2) the yield strength σ of the standard tensile style obtained by this embodiment0It .2 is 500MPa, tensile strength sigmabFor 550MPa, the rate of plastic deformation 10%, intensity are better than the intensity of sample in embodiment 1, and the rate of plastic deformation is close.
Embodiment 3:
One, the ingredient and content of aluminum alloy composition:
Al86Mg10Sc2Zr2, wherein the purity of Al is >=99.9%；The purity of Mg is >=99.5%；Er is by mass percentage For with Al90Er10Or Al80Er20Intermediate alloy form is added；Zr is with Al by mass percentage90Zr10Intermediate alloy form adds Enter.
Two, the preparation step of aluminium alloy molded part:
(1) foundry alloy melting:
With step (1) in embodiment 1.
(2) prepared by powder:
With step (2) in embodiment 1.
(3) preparation of aluminium alloy molded part:
1) threedimensional model of forming parts needed for being established using CAD, and convert thereof into the data format that can be cut；
2) SLM device is imported after threedimensional model being cut into the multilayer with a thickness of 0.05mm together with supporter；
3) high-purity flowing nitrogen is poured into SLM device cabinet, can be carried out when oxygen content in cavity is less than 200ppm Experiment；
4) in one layer of removable substrate upper berth 0.05mm metal powder as described in step S2；
5) geometry of laser scanning step 3) metal powder layer cross section 2 times, laser facula in scanning process are as follows: 0.1mm, the spacing in twice sweep path are as follows: 0.1mm, laser power are as follows: 300W, laser scan rate are as follows: 1000mm/s；
6) substrate declines the thickness of a layer 0.05mm, in the new metal powder in one layer of basal plane upper berth；Laser scanning is newly spread The geometry of metal powder layer cross section 2 times, laser facula are as follows: 0.1mm, the spacing in twice sweep path are as follows: 0.1mm swashs Optical power are as follows: 300W, laser scan rate are as follows: 1000mm/s；Scanning direction and upper one layer of scanning direction rotate clockwise 45 Degree；
7) step 6) is repeated repeatedly, number of repetition is molded part height ÷ powdering thickness -2, after the end of the program, is obtained The aluminium alloy molded part；
(4) it is heat-treated:
Aluminium alloy molded part obtained in step 6) is placed under the conditions of 350 DEG C and is heat-treated 2h, high-performance can be obtained Al86Mg10Sc2Zr2Aluminium alloy molded part.
Three, the Mechanics Performance Testing and beneficial effect of the present embodiment
1, Mechanics Performance Testing:
With embodiment 1.
2, the utility model has the advantages that
It 1) is 99% by the consistency that this embodiment obtains molded part；
2) the yield strength σ 0 of molded samples.2It is 570MPa, the rate of plastic deformation 7% for 530MPa, tensile strength sigma b.
The foregoing is intended to be a preferred embodiment of the present invention.Certainly, the present invention can also have other a variety of implementations Example, without deviating from the spirit and substance of the present invention, anyone skilled in the art, when can according to this Various corresponding equivalent change and modification are made in invention, all should fall within the scope of protection of the appended claims of the present invention.

Claims (9)

1. a kind of Al-Mg-Er-Zr line aluminium alloy, which is characterized in that content is by component by mass percentage: Mg 6-12%, Er 0.5-2%, Zr 0.5-2%, surplus are Al composition, and gross mass percentage is 100%.
2. Al-Mg-Er-Zr line aluminium alloy according to claim 1, which is characterized in that the purity of the Al be >= 99.9% fine aluminium.
3. Al-Mg-Er-Zr line aluminium alloy according to claim 1, which is characterized in that the purity of the Mg be >= 99.5%.
4. Al-Mg-Er-Zr line aluminium alloy according to claim 1, which is characterized in that the Er is by mass percentage With Al90Er10Or Al80Er20Intermediate alloy form is added.
5. Al-Mg-Er-Zr line aluminium alloy according to claim 1, which is characterized in that the Zr is by mass percentage With Al90Zr10Intermediate alloy form is added.
6. a kind of preparation method of Al-Mg-Er-Zr line aluminium alloy as described in any one in claim 1-5, which is characterized in that Include the following steps:
S1: fine aluminium: after crucible is preheated to 500 ± 8 DEG C, by mass percentage, being first placed in crucible by foundry alloy melting, after It is continuous to be warming up to 1200 ± 8 DEG C, after fine aluminium fusing, then by Al90Zr10Intermediate alloy is added in fine aluminium, stirs 50 minutes, wait stir After mixing uniformly, melt temperature is down to 900 ± 5 DEG C, Mg simple substance and Al is then added80Er20Intermediate alloy is stirred 50 minutes, is obtained Obtain ingredient uniform alloy melt；
S2: powder preparation: crucible bottom valve is opened, alloy melt is flowed out through the oxidation aluminum tubular conductor that internal diameter is 10mm, under freedom It falls, liquid stream, at fine drop, forms metal powder after solidification through high pressure nitrogen atomizer impact grinding；
S3: the preparation of aluminium alloy molded part:
1) threedimensional model of forming parts needed for being established using CAD, and convert thereof into the data format that can be cut；
2) SLM device is imported after threedimensional model being cut into the multilayer with a thickness of 0.05mm together with supporter；
3) high pure nitrogen is poured into SLM device cabinet, can be tested when oxygen content in cabinet is less than 200ppm；
4) in one layer of removable substrate upper berth 0.05mm metal powder as described in step S2；
5) geometry of laser scanning step 4) metal powder layer cross section 2 times, laser facula in scanning process are as follows: 0.1mm, The spacing in twice sweep path are as follows: 0.1mm, laser power are as follows: 200-300W, laser scan rate are as follows: 500-1500mm/s；
6) substrate is declined into the thickness that a layer is 0.05mm, in the new metal powder in one layer of substrate upper berth；Laser scanning is newly spread The geometry of metal powder layer cross section 1 time, laser facula in scanning process are as follows: 0.1mm, the spacing in twice sweep path Are as follows: 0.1mm, laser power are as follows: 200-300W, laser scan rate are as follows: 500-1500mm/s, scanning direction and upper one layer scanning Direction rotates clockwise 45 degree；
7) step 6) is repeated repeatedly, number of repetition is molded part height ÷ powdering thickness -2, after the end of the program, is obtained described Aluminium alloy molded part；
S4: heat treatment:
2-12h is heat-treated under the conditions of aluminium alloy molded part obtained in step S3 is placed in 150-300 DEG C to get Al-Mg- is arrived Er-Zr line aluminium alloy molded part.
7. preparation method according to claim 6, which is characterized in that the diameter of metal powder described in step S2 is 20 ~50 microns.
8. preparation method according to claim 6, which is characterized in that the purity of high pure nitrogen described in step S3 is 99.999%.
9. preparation method according to claim 6, which is characterized in that the pressure of atomization described in step S2 is 20MPa.
CN201811354148.XA 2018-11-14 2018-11-14 A kind of Al-Mg-Er-Zr series alloys and preparation method Pending CN109338182A (en)

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