CN111001800A - 3D printing high-strength Al-Cr-Sc alloy - Google Patents

3D printing high-strength Al-Cr-Sc alloy Download PDF

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CN111001800A
CN111001800A CN201911142494.6A CN201911142494A CN111001800A CN 111001800 A CN111001800 A CN 111001800A CN 201911142494 A CN201911142494 A CN 201911142494A CN 111001800 A CN111001800 A CN 111001800A
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alloy
printing
powder
aluminum
metal powder
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CN111001800B (en
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李瑞迪
王银
袁铁锤
李平
牛朋达
王敏卜
***
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SHENZHEN RESEARCH INSTITUTE CENTRAL SOUTH UNIVERSITY
Central South University
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Central South University
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Abstract

The invention discloses a 3D printing high-strength Al-Cr-Sc alloy, wherein the metal powder for the 3D printing high-strength Al-Cr alloy comprises the following components in parts by weight: the metal powder comprises the following components in percentage by mass: cr: 2.5-10%, Mg: 0.5-2.5%, Sc: 0.1 to 0.9%, Zr:0.2～0.7％、Si：0.1～0.3％、Mn：0.2～0.45％、Fe：0.1～0.35％、Ti：0.1～0.25％，AlCl30.05-0.5% of powder and CaCl2+ NaCl: 0.05-0.3% of Al in balance; the preparation method of the metal powder comprises the steps of weighing pure metal block raw materials of Al, Cr, Mg, Sc, Zr, Si, Mn, Fe and Ti, and heating and smelting; atomizing to prepare powder, screening, and preserving heat and drying; adding AlCl3、CaCl2And NaCl powder, and ball milling and mixing, the printed aluminum alloy parts have no cracks, high density, excellent mechanical property, good wear resistance, strong corrosion resistance and excellent high-temperature oxidation resistance.

Description

3D printing high-strength Al-Cr-Sc alloy
Technical Field
The invention belongs to the technical field of design of additive manufacturing 3D printing materials, and particularly relates to a high-strength Al-Cr-Sc alloy for 3D printing.
Background
In recent years, additive manufacturing (commonly known as 3D printing, two processes of specially-made laser selective melting and laser melting deposition in the patent) aluminum alloy is widely regarded as important in the fields of aerospace, rail transit and the like. This is because: first, the conventional processing methods of aluminum alloys are mainly casting, plastic working and welding, and it is difficult to form a member having a complicated shape. With the development of light weight of aerospace and rail transit, aluminum alloy parts with complex topological structure design are difficult to process by adopting a traditional method and need to be processed by adopting a 3D printing technology; secondly, the aluminum alloy of the traditional casting and plastic processing is difficult to prepare the aluminum alloy with the ultrafine grain structure, and the 3D printing can realize the manufacturing of the ultrafine grain aluminum alloy. Thirdly, 3D printing itself is not only a forming technique, but also new materials can be created, as 3D printing is an extreme non-equilibrium preparation means, the solid solubility of solute elements in aluminum alloy can be greatly diffused, thereby preparing or manufacturing metastable aluminum alloy materials.
However, 3D printing of aluminum alloy does not simply use traditional aluminum alloy as raw material to prepare powder by gas atomization, and high-quality printing can be realized. At present, 3D printing of traditional aluminum alloy brands faces the following problems: (1) at present, only 4 series of cast AlSi alloys in the traditional aluminum alloy are suitable for 3D printing, the formability is also good, most of 3D printing aluminum alloys are a series of aluminum-silicon alloys, but the mechanical properties are not high (the tensile is less than 400MPa, and the elongation is less than 6.5%). (2) 3D printing of gas atomized powder of traditional aluminum alloy such as 2-7 series aluminum alloy is easy to generate hot cracks and has poor mechanical property. Therefore, it is necessary to develop an aluminum alloy suitable for a special 3D printing without the concept of the conventional aluminum alloy grade of 2-7 series to some extent.
Disclosure of Invention
This section is for the purpose of summarizing some aspects of embodiments of the invention and to briefly introduce some preferred embodiments. In this section, as well as in the abstract and the title of the invention of this application, simplifications or omissions may be made to avoid obscuring the purpose of the section, the abstract and the title, and such simplifications or omissions are not intended to limit the scope of the invention.
The present invention has been made in view of the above-mentioned technical drawbacks.
Therefore, as one aspect of the present invention, the present invention overcomes the shortcomings of the prior art and provides a 3D printed high strength Al-Cr-Sc alloy.
In order to solve the technical problems, the invention provides the following technical scheme: the utility model provides a 3D prints metal powder for high strength aluminium chrome alloy, it includes, by mass percent, the metal powder is gas atomization pre-alloyed powder, includes: cr: 4.5-6.5%, Mg: 1.5-2.0%, Sc: 0.5 to 1.2%, Zr: 0.2 to 0.35%, Si: 0.2-0.3%, Mn: 0.25 to 0.35%, Fe: 0.2 to 0.3%, Ti: 0.15-0.2%, AlCl3 powder: 0.1-0.25%, CaCl2+ NaCl: 0.1-0.2%, and the balance of Al.
In one aspect of the invention, the invention overcomes the defects in the prior art and provides a metal for 3D printing of high-strength aluminum-chromium alloyA method of preparing a powder comprising: weighing Al, AlCr intermediate alloy, Mg, AlSc intermediate alloy, AlZr intermediate alloy, AlSi intermediate alloy, AlMn intermediate alloy, AlFe intermediate alloy and AlTi intermediate alloy according to the mass percentage, and heating and smelting; atomizing to prepare powder, screening, and preserving heat and drying; adding AlCl3、CaCl2And NaCl powder, ball milling, mixing and drying; wherein, by mass percentage, the Cr is 2.5-10%, the Mg is 0.5-2.5%, the Sc is 0.1-1.8%, the Zr is 0.2-0.7%, the Si is 0.1-0.3%, the Mn is 0.2-0.45%, the Fe is 0.1-0.35%, the Ti is 0.1-0.25%, and the AlCl is30.05-0.5% of CaCl2And 0.05-0.3% of NaCl, and the balance of Al.
The preferable scheme of the preparation method of the metal powder for the 3D printing high-strength aluminum-chromium alloy is that: the heating and melting are carried out in a vacuum induction furnace, the air pressure is 0.8MPa, the melting temperature is 850 ℃, the atomization powder preparation is carried out by utilizing helium, the atomization air pressure is 8MPa, the heat preservation and drying are carried out, the heat preservation time is 12 hours, and the drying temperature is 95 ℃.
The preferable scheme of the preparation method of the metal powder for the 3D printing high-strength aluminum-chromium alloy is that: the Cr element in the aluminum-chromium alloy forms a supersaturated solid solution under the special rapid cooling condition of 3D printing, and the solid solution content of the Cr element in the aluminum alloy matrix is enhanced, so that the tensile strength and the corrosion resistance of the aluminum alloy are enhanced, and the segregation of the Cr element in a crystal boundary under a special application environment is reduced. So that the Al-Cr alloy which can not be prepared by the traditional casting process becomes practical in the invention.
The preferable scheme of the preparation method of the metal powder for the 3D printing high-strength aluminum-chromium alloy is that: the addition of Ti and Fe elements in the aluminum-chromium alloy aims to form a long-range ordered periodic structure under the condition of special rapid cooling of 3D printing, so that the effect of strengthening and toughening is achieved, meanwhile, the addition of Fe elements can achieve the effect of solid solution strengthening, the stacking fault energy of the alloy is reduced, and high-density stacking faults and twin crystals are formed.
The preferable scheme of the preparation method of the metal powder for the 3D printing high-strength aluminum-chromium alloy is that: the aluminum-chromium alloy is added with high-content Mg and Mn elements, and the main purpose is two aspects, namely, the first aspect is to form supersaturated solid solution and greatly improve the effect of solid solution strength; secondly, the intermetallic compound is formed with Al element to control the recrystallization process, refine crystal grains, reduce the generation of residual stress and greatly reduce the sensitivity of crack generation in the 3D printing process of the alloy.
The preferable scheme of the preparation method of the metal powder for the 3D printing high-strength aluminum-chromium alloy is that: sc and Zr elements are added into the aluminum-chromium alloy, and the main purpose is to precipitate Al3The (Sc, Zr) phase has good thermal stability and grain growth inhibition effect, so that the growth of grains and the generation of large columnar crystals in a molten pool can be inhibited in the printing process, the generation and the propagation of cracks are greatly inhibited, and the (Sc, Zr) phase plays a role of a crack inhibitor.
The preferable scheme of the preparation method of the metal powder for the 3D printing high-strength aluminum-chromium alloy is that: the aluminum-chromium alloy not only considers the independent action of each element, but also considers the synergistic action among the elements, and firstly, Fe and Mn elements form intermetallic compounds to hinder the growth process of crystal grains in the printing process; secondly, Si and Mg form eutectic and strengthening phases, the solidification temperature range of the alloy is reduced, the cracking sensitivity of the alloy in the solidification later stage in the printing process is reduced, and the like, AlCl3、CaCl2And the NaCl powder has the main functions of solving the generation of oxide particles and hydrogen holes in a molten pool, improving the compactness of the alloy and reducing the oxides.
As another aspect of the present invention, the present invention provides a new use of a high strength aluminum chrome alloy for 3D printing, characterized in that the metal powder is used for 3D printing, and heat treatment is performed by a pulsed current; wherein the heat treatment is carried out by pulse current, the pulse current is introduced, and the current density is 230A/cm2The heat treatment temperature is 300 ℃, the heating speed is 50 ℃/min, the heat preservation time is 1h, the temperature is controlled to be within the range ofPulse current is introduced in the heat treatment process, so that low-temperature heat treatment can be realized, and Si and Al are ensured3Zr/Al3Sc、(Cr,Fe)Al7And (Cr, Mn) Al12The equal phase precipitation forms the functions of precipitation strengthening and dispersion strengthening, and stabilizes the grain size in the heat treatment process.
As a preferable scheme of the application of the metal powder for 3D printing of the high-strength aluminum-chromium alloy, the metal powder comprises the following components: the laser parameters for 3D printing are as follows: the preheating temperature of the printing substrate is 200 ℃; the laser scanning power is 250W; the laser scanning speed is 650 mm/s; the scanning distance is 0.05 mm; the interlayer thickness is 0.05 mm; the density of the printed part reaches 99.5 percent, no crack exists, the tensile strength reaches 530MPa, the elongation reaches 15 percent, and the average hardness reaches 157HV0.2The high-temperature-resistant composite material has the advantages of fine and uniform structure, no crack, high density, low anisotropy, excellent corrosion resistance and high-temperature oxidation resistance, and can be widely applied to the manufacture of aerospace, automobile parts and mechanical parts with strict environmental requirements.
The invention relates to a design basis of the element components of metal powder for 3D printing of high-strength aluminum-chromium alloy, wherein the design basis comprises the following steps:
a) function of Cr element: under the condition of 3D printing and rapid cooling, a supersaturated solid solution is formed, and the solid solution content of Cr element in an aluminum alloy matrix is increased, so that the tensile strength and the corrosion resistance of the aluminum alloy are enhanced; meanwhile, the Fe-Mn alloy forms an intermetallic compound with Fe and Mn elements, and crystal grain growth in the printing process is hindered.
b) The effect of Sc and Zr elements: the addition of Sc and Zr mainly plays a role in eliminating textures and refining grains in the printing process, reduces the sensitivity of crack generation in the 3D printing process, forms supersaturated solid solution in aluminum alloy, and has good thermal stability and the function of inhibiting the growth of grains of the precipitated Al3(Sc and Zr) phase.
c) Function of Fe and Ti elements: the method mainly plays a role in solid solution strengthening, reduces the stacking fault energy of the alloy, forms high-density stacking faults and twin crystals, and simultaneously plays a toughening effect because a long-range ordered periodic structure is formed in the nonequilibrium process of 3D printing.
d) Function of Si element: the addition of the Si element can reduce the solidification temperature range of the alloy, so that the existence of a large amount of liquid can be ensured at the final solidification stage, the intergranular interval can be filled more easily, the capability of healing initial cracks is improved, and meanwhile, the effects of solid solution strengthening and precipitation dispersion strengthening (Mg2Si strengthening phase precipitation) are achieved.
e) Effect of Mg and Mn elements: high-content Mg and Mn elements are added into the aluminum-chromium alloy, and the main purpose is two aspects, namely, the first is to form supersaturated solid solution and greatly improve the effect of solid solution strength; secondly, the intermetallic compound is formed with Al element to control the recrystallization process, refine the crystal grains and reduce the crack sensitivity.
f) Effect of AlCl3, CaCl2 and NaCl: AlCl3The CaCl2 and NaCl powder are added to solve the problem of oxide particles and hydrogen holes in the molten pool, improve the compactness of the alloy and reduce the oxide. The addition of the elements starts from the strength of the material, the reduction of crack sensitivity in the printing process and the elimination of oxide particles and oxides in the molten pool, and simultaneously takes the strengthening of the elements into consideration, thereby showing the synergistic enhancement effect.
The invention has the beneficial effects that:
first, the theoretical solid solubility of Cr in Al is less than 1.5 wt%, so that conventional melting and casting cannot produce Al-Cr solid solution alloys with high Cr content (more than 2.5 wt%), whereas the present invention can produce Al-Cr alloys relatively easily using the rapid solidification effect of 3D printing, in which the Cr content exceeds 2.5 wt%, making Al-Cr alloys that cannot be produced by conventional melting and casting processes practical in the present invention. Secondly, the components of the traditional aluminum-chromium alloy are improved, so that the cracking phenomenon of the traditional aluminum-chromium alloy in 3D printing and the defects of poor mechanical property and high anisotropy are overcome; thirdly, by combining the prepared new aluminum-chromium alloy components with optimal 3D printing process parameters, the prepared parts have the advantages of fine and uniform tissue, no crack, high density, low anisotropy, tensile strength of 530MPa, average hardness of more than 157HV0.2 and elongation of 15 percent after aging, and simultaneously show excellent corrosion resistance and high-temperature oxidation resistance; fourthly, the heat treatment in the invention adopts a mode of pulse current introduction for heat treatment, which can stably maintain the original printing fine grain structure, and simultaneously has better effect and increased precipitated phases compared with the traditional heat treatment mode. The high-strength aluminum-chromium alloy printed by the method can be widely applied to manufacturing of aerospace, automobile parts and mechanical parts with strict environmental requirements.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings needed to be used in the description of the embodiments will be briefly introduced below, and it is obvious that the drawings in the following description are only some embodiments of the present invention, and it is obvious for those skilled in the art to obtain other drawings based on these drawings without inventive exercise. Wherein:
FIG. 1 is a scanning topography of a 3D printed high strength aluminum chromium alloy powder prepared in example 1;
FIG. 2 is a gold phase diagram of the 3D printed high strength aluminum chromium alloy powder prepared in example 1;
FIG. 3 is a metallographic image of a 3D printed high strength aluminum chromium alloy part prepared in example 1 after corrosion;
FIG. 4 is a metallographic image of the 3D printed high strength aluminum chromium alloy part prepared in example 2 after corrosion.
Detailed Description
In order to make the aforementioned objects, features and advantages of the present invention comprehensible, embodiments accompanied with examples are described in detail below.
In the following description, numerous specific details are set forth in order to provide a thorough understanding of the present invention, but the present invention may be practiced in other ways than those specifically described and will be readily apparent to those of ordinary skill in the art without departing from the spirit of the present invention, and therefore the present invention is not limited to the specific embodiments disclosed below.
Furthermore, reference herein to "one embodiment" or "an embodiment" means that a particular feature, structure, or characteristic described in connection with the embodiment is included in at least one implementation of the invention. The appearances of the phrase "in one embodiment" in various places in the specification are not necessarily all referring to the same embodiment, nor are separate or alternative embodiments mutually exclusive of other embodiments.
Example 1:
the special high-strength aluminum-chromium alloy composition for 3D printing, which is prepared by the invention, comprises the following components in percentage by mass: cr: 4.5%, Mg: 1.5%, Sc: 0.65%, Zr: 0.2%, Si: 0.2%, Mn: 0.25%, Fe: 0.2%, Ti: 0.15% of AlCl3Powder: 0.14 percent; CaCl2+ NaCl: 0.16% and the balance of Al.
The preparation method of the aluminum alloy powder comprises the following steps:
(1) smelting raw materials: removing AlCl3、CaCl2And weighing the intermediate compound metal block raw material and other elements except NaCl powder according to a proportion, putting the raw material into a vacuum induction furnace for heating and smelting, wherein the air pressure in the vacuum induction furnace is 0.8MPa, and the smelting temperature is 850 ℃.
(2) Atomizing to prepare powder: and transferring the smelted prealloy metal into an atomization tank, and carrying out atomization powder preparation by using helium, wherein the atomization pressure is 8 MPa.
(3) Powder screening: and (3) screening the pre-alloyed metal powder to obtain metal powder with the average particle size of 29.5 microns, wherein the particle size range is 15-35.7 microns.
(4) And (3) heat preservation and drying: and (3) placing the sieved powder into a drying box, and keeping the temperature for 12 hours at the drying temperature of 95 ℃.
AlCl3、CaCl2And finally adding NaCl powder into the pre-alloyed powder in a ball milling mechanical mixing mode, and fully ball milling and mixing, wherein the powder morphology is as shown in figures 1 and 2, the sphericity is high, the amount of adsorbed satellite powder is small, the fluidity is good, and the powder requirement of 3D printing is met.
The laser parameters of the powder for 3D printing are as follows: the preheating temperature of the printing substrate is 200 ℃; the laser scanning power is 250W; the laser scanning speed is 650 mm/s; the scanning distance is 0.05 mm; the interlayer thickness was 0.05 mm.
Menstrual heatAnd (3) treatment: pulse current is introduced, and the current density is 230A/cm2The heat treatment temperature is 300 ℃, the heating speed is 50 ℃/min, and the heat preservation time is 1 h; the aluminum-chromium alloy powder for 3D printing has good powder sphericity, strong fluidity and small powder particle size, and the powder morphology is shown in figures 1 and 2. After electrochemical corrosion, the microstructure is shown in figure 3, the microstructure is obvious at present, no obvious crack exists, almost no hole defect exists, and the density is high; through mechanical property tests of parts, the compactness reaches 99.5 percent, the tensile strength reaches 510MPa, and the average hardness is 166HV0.2Above, the elongation rate reaches 15 percent; in a corrosion performance test, compared with aluminum-silicon and other series of alloys, the corrosion resistance is stronger and the oxidation resistance is more excellent by testing the polarization curve.
Example 2:
the special high-strength aluminum-chromium alloy composition for 3D printing, which is prepared by the invention, comprises the following components in percentage by mass: cr: 5%, Mg: 1.7%, Sc: 0.75%, Zr: 0.25%, Si: 0.24%, Mn: 0.28%, Fe: 0.24%, Ti: 0.17% of AlCl3Powder: 0.18%, CaCl2+ NaCl: 0.17% and the balance Al.
The preparation method of the aluminum alloy powder comprises the following steps:
(1) smelting raw materials: removing AlCl3、CaCl2And weighing the intermediate compound metal block raw materials in proportion except the NaCl powder, and putting the intermediate compound metal block raw materials into a vacuum induction furnace for heating and smelting.
(2) Atomizing to prepare powder: and transferring the smelted prealloy metal into an atomization tank, and carrying out atomization powder preparation by using helium.
(3) Powder screening: and (3) screening the pre-alloyed metal powder to obtain metal powder with the average particle size of 28.4 microns, wherein the particle size range is 14-36.1 microns.
(4) And (3) heat preservation and drying: and (3) placing the sieved powder into a drying box, and keeping the temperature for 12 hours at the drying temperature of 95 ℃.
AlCl3、CaCl2And finally adding NaCl powder into the prealloyed powder in a mixing mode, and fully ball-milling and mixing.
The laser parameters of the powder for 3D printing are as follows: the preheating temperature of the printing substrate is 200 ℃; the laser scanning power is 250W; the laser scanning speed is 650 mm/s; the scanning distance is 0.05 mm; the interlayer thickness was 0.05 mm.
Carrying out heat treatment: pulse current is introduced, and the current density is 230A/cm2The heat treatment temperature is 300 ℃, the heating speed is 50 ℃/min, and the heat preservation time is 1 h; after corrosion, the microstructure is shown in fig. 4, no crack or hole defect is found, the microstructure is obvious, and the density is high; in a density test, the density reaches 99.5 percent, and meanwhile, the high-strength high-toughness high-strength high-toughness high0.2And simultaneously has excellent oxidation resistance and corrosion resistance.
Example 3:
the special high-strength aluminum-chromium alloy composition for 3D printing, which is prepared by the invention, comprises the following components in percentage by mass: cr: 6%, Mg: 1.9%, Sc: 0.80%, Zr: 0.28%, Si: 0.27%, Mn: 0.3%, Fe: 0.27%, Ti: 0.19%, AlCl3 powder: 0.22%, CaCl2+ NaCl: 0.18 percent and the balance of Al.
The preparation method of the aluminum alloy powder comprises the following steps:
(1) smelting raw materials: removing AlCl3、CaCl2And weighing the intermediate compound metal block raw materials in proportion except the NaCl powder, and putting the intermediate compound metal block raw materials into a vacuum induction furnace for heating and smelting.
(2) Atomizing to prepare powder: and transferring the smelted prealloy metal into an atomization tank, and carrying out atomization powder preparation by using helium.
(3) Powder screening: and (3) screening the pre-alloyed metal powder to obtain the metal powder with the average grain diameter of 30.1 microns, wherein the grain diameter ranges from 16.1 microns to 34.2 microns.
(4) And (3) heat preservation and drying: and (3) placing the sieved powder into a drying box, and keeping the temperature for 12 hours at the drying temperature of 95 ℃.
AlCl3、CaCl2And NaCl powder is finally added to the above pre-mix in a mixed mannerAnd fully ball-milling and mixing the alloy powder.
The laser parameters of the powder for 3D printing are as follows: the preheating temperature of the printing substrate is 200 ℃; the laser scanning power is 250W; the laser scanning speed is 650 mm/s; the scanning distance is 0.05 mm; the interlayer thickness was 0.05 mm.
Carrying out heat treatment: pulse current is introduced, and the current density is 230A/cm2The heat treatment temperature is 300 ℃, the heating speed is 50 ℃/min, the heat preservation time is 1h, the density reaches 99.3 percent, no crack exists, the tensile strength reaches 535MPa, the elongation rate is 14 percent, and the average hardness is 187HV0.2And has excellent oxidation resistance and corrosion resistance.
Example 4:
the special high-strength aluminum-chromium alloy composition for 3D printing, which is prepared by the invention, comprises the following components in percentage by mass: cr: 6.5%, Mg: 2.0% and Sc: 0.85%, Zr: 0.33%, Si: 0.3%, Mn: 0.3%, Fe: 0.3%, Ti: 0.2%, AlCl3 powder: 0.25%, CaCl2+ NaCl: 0.2% and the balance Al.
The preparation method of the aluminum alloy powder comprises the following steps:
(1) smelting raw materials: removing AlCl3、CaCl2Weighing the intermediate compound metal block raw materials in proportion except the NaCl powder, and putting the raw materials into a vacuum induction furnace for heating and smelting;
(2) atomizing to prepare powder: transferring the smelted prealloy metal into an atomization tank, and carrying out atomization powder preparation by using helium;
(3) powder screening: and (3) screening the pre-alloyed metal powder to obtain metal powder with the average particle size of 29.1 microns, wherein the particle size range is 14.8 microns-34.6 microns.
(4) And (3) heat preservation and drying: and (3) placing the sieved powder into a drying box, and keeping the temperature for 12 hours at the drying temperature of 95 ℃.
AlCl3、CaCl2And finally adding NaCl powder into the prealloyed powder in a mixing mode, and fully ball-milling and mixing.
The laser parameters of the powder for 3D printing are as follows: the preheating temperature of the printing substrate is 200 ℃; the laser scanning power is 250W; the laser scanning speed is 650 mm/s; the scanning distance is 0.05 mm; the interlayer thickness was 0.05 mm.
Carrying out heat treatment: pulse current is introduced, and the current density is 230A/cm2The heat treatment temperature is 300 ℃, the heating speed is 50 ℃/min, the heat preservation time is 1h, the density reaches 99.6 percent, no crack exists, the tensile strength reaches 540MPa, the elongation is 15 percent, and the average hardness is 188HV0.2And has excellent oxidation resistance and corrosion resistance.
Example 5:
the Cr content and the Mg content in example 3 were adjusted to 1.5 wt% and 0.2 wt%, respectively, and the other preparation conditions were the same as in example 3, and it was found that the tensile strength of the product was 350MPa, the elongation was 7%, many cracks were generated, the density was reduced, the effect of the trace elements was lost, and the hardness was reduced to 95HV0.2。
Example 6:
the Cr content and the Mg content in example 3 were adjusted to 15 wt% and 4 wt%, respectively, and the other preparation conditions were the same as in example 3, and the tensile strength of the product was 405MPa, the elongation was 8%, cracks were generated, the density was low, and the hardness was 104HV0.2。
Example 7:
AlCl in example 33And CaCl2The content of + NaCl was adjusted to 0.01 wt% and 0.02 wt%, respectively, and the other preparation conditions were the same as in example 3, and the tensile strength of the product was found to be 514MPa, and black oxide particles appeared inside the molten pool in the observation of the microstructure, and the density was reduced with a small amount of hydrogen pores.
Example 8:
selecting the raw material proportion in the embodiment 3, adjusting the laser power in the printing parameters to be 100W, and keeping the preparation conditions the same as those of the embodiment 3, wherein the surface of the printing part is attached with a large amount of spherical powder and has large roughness; in metallographic observation, a large amount of particles of the unmelted metal powder are also found, cracks appear in the molten pool, and the mechanical properties are poor.
Example 9:
optional embodiment 3Raw material proportioning, namely adjusting the laser power in the printing parameters to 500W, wherein the rest preparation conditions are the same as those in the embodiment 3; in metallographic microstructure observation, spherical hydrogen pores and volatilized element pores appear in the molten pool, and black oxide is generated due to high laser power; in a tensile test, the tensile strength of the part is 320MPa, the elongation is 5 percent, cracks are generated, the density is low, and the hardness is 98HV0.2By comparison of the mechanical properties, the printing proper parameters are thus selected according to the optimum.
Example 10:
the raw material proportion in example 3 is selected, the heat treatment temperature is adjusted to 150 ℃, the current density is invariable, the original parameters are still kept, the other preparation conditions are the same as those in example 3, a small amount of hard phase is precipitated, and the measured tensile strength of the part is 490MPa, the elongation is 10 percent, and the hardness is 140HV0.2。
Example 11:
the raw material proportion in example 3 is selected, the heat treatment temperature is adjusted to 400 ℃, the current density is invariable, the original parameters are still kept, the other preparation conditions are the same as those in example 3, in the observation of microstructure, precipitated phases and crystal grains are found to be enlarged, the tensile strength of the part is 530MPa, the elongation is 11 percent, and the hardness is 164HV0.2The mechanical property is reduced compared with the optimal heat treatment temperature, so that 300 ℃ is adopted as the optimal heat treatment temperature after electrification.
Table 1 shows the statistics of the mechanical properties of all examples
Figure BDA0002281329980000101
The Cr element in the aluminum-chromium alloy forms a supersaturated solid solution under the special rapid cooling condition of 3D printing, the solid solution content of the Cr element in an aluminum alloy matrix is enhanced, so that the tensile strength and the corrosion resistance of the aluminum alloy are enhanced, and the segregation of the Cr element in a crystal boundary under special application environments, such as intergranular corrosion of parts in high-temperature environments of engines of airplanes and the like and tropical marine environments, is reduced, so that the traditional melting method is used for melting the Cr element in the aluminum-chromium alloyThe Al-Cr alloy which cannot be prepared by the casting process becomes a reality in the invention; forming an intermetallic compound with Fe and Mn elements to prevent the growth of crystal grains in the printing process; the addition of Ti and Fe elements aims at forming a long-range ordered periodic structure under the condition of special rapid cooling of 3D printing, and plays a role in strengthening and toughening, and meanwhile, the addition of Fe elements can play a role in solid solution strengthening, so that the stacking fault energy of the alloy is reduced, and high-density stacking faults and twin crystals are formed; high-content Mg and Mn elements are added into the aluminum-chromium alloy, and the main purpose is two aspects, namely, the first is to form supersaturated solid solution and greatly improve the effect of solid solution strength; secondly, an intermetallic compound is formed with Al element to control the recrystallization process, refine crystal grains, reduce the generation of residual stress and reduce the sensitivity of crack generation in the 3D printing process of the alloy to a great extent; because of the special processing process of 3D printing, the printing of the later layer can perform one-time heat treatment on the former layer, so Sc and Zr elements are added into the aluminum-chromium alloy, and the main purpose is to form supersaturated solid solution in the aluminum alloy and precipitate Al3The (Sc, Zr) phase has good thermal stability and grain growth inhibition effect, so that the growth of grains and the generation of large columnar crystals in a molten pool can be inhibited in the printing process, the effects of eliminating textures and refining the grains are achieved, the generation and the propagation of cracks are greatly inhibited, and the effect of a crack inhibitor is achieved.
According to the alloy formula, not only are the individual effects of all elements considered, but also the synergistic effect among the elements is excavated, and firstly, Fe and Mn elements form an intermetallic compound, so that the growth process of crystal grains is hindered in the printing process; secondly, the addition of the Si element can reduce the solidification temperature range of the alloy, so that the existence of a large amount of liquid can be ensured at the final solidification stage, the intergranular region can be filled more easily, the capability of healing initial cracks can be improved, and meanwhile, the effects of solid solution strengthening and precipitation dispersion strengthening (Mg2Si strengthening phase precipitation) are achieved; si and Mg form eutectic and strengthening phases, the solidification temperature range of the alloy is reduced, and the cracking sensitivity of the alloy in the later solidification period in the printing process is reduced; AlCl3、CaCl2And NaCl powder mainly for solving the molten poolThe generation of oxide particles and hydrogen holes improves the density of the alloy and reduces the generation of oxides. The addition of the elements starts from the strength of the material, the reduction of crack sensitivity in the printing process and the elimination of oxide particles and oxides in the molten pool, and simultaneously takes the strengthening of the elements into consideration, thereby showing the synergistic enhancement effect.
In conclusion, the proper percentage of Mg, Sc, Zr, Si, Mn, Fe, Ti and AlCl is added into the aluminum-chromium alloy3And CaCl2The cracking sensitivity of the 3D printed aluminum-chromium alloy is greatly reduced due to microelements such as NaCl, meanwhile, due to a special forming mechanism of the 3D printing, the elements in the aluminum-chromium alloy are more suitable for the special purpose of the 3D printing, the mechanical property of the printed part is excellent, the structure is fine and uniform, no crack exists, the density is high, the anisotropy is low, the highest tensile strength reaches 570MPa, the highest elongation reaches 15%, and the average hardness reaches 188HV0.2And has good corrosion resistance and high-temperature oxidation resistance. The high-strength aluminum-chromium alloy printed by the method can be widely applied to manufacturing of aerospace, automobile parts and mechanical parts with strict environmental requirements.
The invention further prefers a heat treatment mode, pulse current is introduced in the heat treatment process, the low-temperature heat treatment can be realized, and the current density is 230A/cm2The heat treatment temperature is 300 ℃, the heating speed is 50 ℃/min, the heat preservation time is 1h, the original printed fine grain structure can be stably kept, the effect is better than that of the traditional heat treatment mode, and the precipitated phases are increased. And aging and quenching the 3D printed parts to obtain the final product. In the present invention, the purpose of performing the subsequent heat treatment is to select the optimum heat treatment method to ensure that Si and Al are present3Zr/Al3Sc、(Cr,Fe)Al7And (Cr, Mn) Al12The equal phase precipitation forms the functions of precipitation strengthening and dispersion strengthening, and stabilizes the grain size in the heat treatment process.
The method subverts the traditional thought, creates a new material by utilizing the extremely rapid non-equilibrium solidification characteristic of 3D printing, and can easily prepare the Al-Cr alloy, wherein the Cr content exceeds 2.5-3.5 wt%.. In the Al-Cr alloy printed by laser 3D, Cr can be completely dissolved in an Al matrix by laser rapid solidification, so that the solid solubility of Cr in Al is greatly improved without precipitation. By adding proper percentages of Mg, Sc, Zr, Si, Mn, Fe, Ti and AlCl into the aluminum-chromium alloy3And CaCl2The cracking sensitivity of the 3D printed aluminum-chromium alloy is greatly reduced due to microelements such as NaCl, meanwhile, due to a special forming mechanism of the 3D printing, the elements in the aluminum-chromium alloy are more suitable for the special purpose of the 3D printing, the mechanical property of the printed part is excellent, the structure is fine and uniform, no crack exists, the density is high, the anisotropy is low, the highest tensile strength reaches 565MPa, the highest elongation reaches 15%, and the average hardness reaches 187HV0.2And has good corrosion resistance and high-temperature oxidation resistance. Compared with the existing mature 3D printing Al-Si alloy system, the 3D printing Al-Cr alloy system has higher mechanical strength and excellent corrosion resistance, the designed components are specially used for 3D printing and forming, and the printed aluminum alloy parts have the advantages of no cracks, high density, excellent mechanical property after optimal heat treatment, good wear resistance, strong corrosion resistance and excellent high-temperature oxidation resistance. The high-strength aluminum-chromium alloy printed by the method can be widely applied to manufacturing of aerospace, automobile parts and mechanical parts with strict environmental requirements.
The invention provides a method for preparing an Al-Cr alloy with supersaturated solid solution by adopting laser 3D printing and rapid solidification, which greatly improves the solid solubility of Cr in Al. The invention has the following steps: the theoretical solid solubility of Cr in Al is lower than 1.5 wt%, so that the conventional smelting and casting cannot prepare Al-Cr solid solution alloy with high Cr content (more than 2.5 wt%), while the invention can easily prepare Al-Cr alloy with Cr content more than 2.5 wt% by using the rapid solidification effect of 3D printing. Compared with the existing mature 3D printing Al-Si alloy system, the 3D printing Al-Cr alloy system has higher mechanical strength and excellent corrosion resistance, the designed components are specially used for 3D printing and forming, and the printed aluminum alloy parts have the advantages of no cracks, high density, excellent mechanical property after optimal heat treatment, good wear resistance, strong corrosion resistance and excellent high-temperature oxidation resistance.
It should be noted that the above-mentioned embodiments are only for illustrating the technical solutions of the present invention and not for limiting, and although the present invention has been described in detail with reference to the preferred embodiments, it should be understood by those skilled in the art that modifications or equivalent substitutions may be made on the technical solutions of the present invention without departing from the spirit and scope of the technical solutions of the present invention, which should be covered by the claims of the present invention.

Claims (10)

1. The utility model provides a 3D prints metal powder for high strength Al-Cr-Sc alloy which characterized in that:
the metal powder is gas atomization pre-alloy powder and comprises the following components in percentage by mass: cr: 2.5-10%, Mg: 0.5-2.5%, Sc: 0.1 to 1.8%, Zr: 0.2 to 0.7%, Si: 0.1-0.3%, Mn: 0.2-0.45%, Fe: 0.1 to 0.35%, Ti: 0.1-0.25% of AlCl30.05-0.5% of powder and CaCl2+ NaCl: 0.05-0.3%, and the balance of Al.
2. A preparation method of metal powder for 3D printing of high-strength aluminum-chromium alloy is characterized by comprising the following steps:
weighing Al, AlCr intermediate alloy, Mg, AlSc intermediate alloy, AlZr intermediate alloy, AlSi intermediate alloy, AlMn intermediate alloy, AlFe intermediate alloy and AlTi intermediate alloy according to the mass percentage, and heating and smelting;
atomizing to prepare powder, screening, and preserving heat and drying;
adding AlCl3、CaCl2And NaCl powder, and ball milling and mixing;
wherein, by mass percentage, the Cr is 2.5-10%, the Mg is 0.5-2.5%, the Sc is 0.1-1.8%, the Zr is 0.2-0.7%, the Si is 0.1-0.3%, the Mn is 0.2-0.45%, the Fe is 0.1-0.35%, the Ti is 0.1-0.25%, and the AlCl is30.05-0.5% of CaCl2And 0.05-0.3% of NaCl, and the balance of Al.
3. The method of preparing metal powder for 3D printing high strength aluminum chromium alloy as claimed in claim 2, wherein: the heating and melting are carried out in a vacuum induction furnace, the air pressure is 0.8MPa, the melting temperature is 850 ℃, the atomization powder preparation is carried out by utilizing helium, the atomization air pressure is 8MPa, the heat preservation and drying are carried out, the heat preservation time is 12 hours, and the drying temperature is 95 ℃.
4. The method for preparing metal powder for 3D printing of high-strength aluminum-chromium alloy according to claim 2 or 3, characterized in that: the Cr element in the aluminum-chromium alloy forms a supersaturated solid solution under the special rapid cooling condition of 3D printing, and the solid solution content of the Cr element in the aluminum alloy matrix is enhanced, so that the tensile strength and the corrosion resistance of the aluminum alloy are enhanced, and the segregation of the Cr element in a crystal boundary under a special application environment is reduced. So that the Al-Cr alloy which can not be prepared by the traditional casting process becomes practical in the invention.
5. The method for preparing metal powder for 3D printing of high-strength aluminum-chromium alloy according to claim 2 or 3, characterized in that: the addition of Ti and Fe elements in the aluminum-chromium alloy aims to form a long-range ordered periodic structure under the condition of special rapid cooling of 3D printing, so that the effect of strengthening and toughening is achieved, meanwhile, the addition of Fe elements can achieve the effect of solid solution strengthening, the stacking fault energy of the alloy is reduced, and high-density stacking faults and twin crystals are formed.
6. The method for preparing metal powder for 3D printing of high-strength aluminum-chromium alloy according to claim 2 or 3, characterized in that: the aluminum-chromium alloy is added with high-content Mg and Mn elements, and the main purpose is two aspects, namely, the first aspect is to form supersaturated solid solution and greatly improve the effect of solid solution strength; secondly, the intermetallic compound is formed with Al element to control the recrystallization process, refine crystal grains, reduce the generation of residual stress and greatly reduce the sensitivity of crack generation in the 3D printing process of the alloy.
7. 3D printing high strength aluminum chrome as claimed in claim 2 or 3A method for preparing metal powder for gold, which is characterized in that: sc and Zr elements are added into the aluminum-chromium alloy, and the main purpose is to precipitate Al3The (Sc, Zr) phase has good thermal stability and grain growth inhibition effect, so that the growth of grains and the generation of large columnar crystals in a molten pool can be inhibited in the printing process, the generation and the propagation of cracks are greatly inhibited, and the (Sc, Zr) phase plays a role of a crack inhibitor.
8. The method for preparing metal powder for 3D printing of high-strength aluminum-chromium alloy according to claim 2 or 3, characterized in that: the aluminum-chromium alloy not only considers the independent action of each element, but also considers the synergistic action among the elements, and firstly, Fe and Mn elements form intermetallic compounds to hinder the growth process of crystal grains in the printing process; secondly, Si and Mg form eutectic and strengthening phases, the solidification temperature range of the alloy is reduced, the cracking sensitivity of the alloy in the solidification later stage in the printing process is reduced, and the like, AlCl3、CaCl2And the NaCl powder has the main functions of solving the generation of oxide particles and hydrogen holes in a molten pool, improving the compactness of the alloy and reducing the oxides.
9. The application of the metal powder for 3D printing of the high-strength aluminum-chromium alloy according to any one of claims 1 to 3 is characterized in that: 3D printing is carried out by utilizing the metal powder, and heat treatment is carried out by pulse current; wherein the heat treatment is carried out by pulse current, the pulse current is introduced, and the current density is 230A/cm2The heat treatment temperature is 300 ℃, the heating speed is 50 ℃/min, the heat preservation time is 1h, and pulse current is introduced in the heat treatment process, so that the low-temperature heat treatment can be realized, and Si and Al are ensured3Zr/Al3Sc、(Cr,Fe)Al7And (Cr, Mn) Al12The equal phase precipitation forms the functions of precipitation strengthening and dispersion strengthening, and stabilizes the grain size in the heat treatment process.
10. Use of a metal powder for 3D printing of high strength aluminium chrome alloy according to claim 9, characterized in that: the laser parameters for 3D printing are as follows: the preheating temperature of the printing substrate is 200 ℃; the laser scanning power is 250W; the laser scanning speed is 650 mm/s; the scanning distance is 0.05 mm; the interlayer thickness is 0.05 mm;
the density of the printed part reaches 99.5 percent, no crack exists, the tensile strength reaches 530MPa, the elongation reaches 15 percent, and the average hardness reaches 157HV0.2The high-temperature-resistant composite material has the advantages of fine and uniform structure, no crack, high density, low anisotropy, excellent corrosion resistance and high-temperature oxidation resistance, and can be widely applied to the manufacture of aerospace, automobile parts and mechanical parts with strict environmental requirements.
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Cited By (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111531172A (en) * 2020-05-29 2020-08-14 同济大学 3D printing process method of high-strength aluminum-silicon alloy
CN111659889A (en) * 2020-06-30 2020-09-15 同济大学 3D printing process method of high-strength aluminum-manganese alloy
CN111673085A (en) * 2020-06-30 2020-09-18 同济大学 3D printing process method of high-strength aluminum-magnesium-silicon alloy
CN112620649A (en) * 2020-11-30 2021-04-09 华中科技大学 Aluminum alloy material and laser 3D printing aluminum alloy component based on same
CN112813310A (en) * 2020-06-28 2021-05-18 中南大学 High-strength Al-Fe-Sc alloy capable of being used for laser additive manufacturing
CN113042729A (en) * 2021-03-16 2021-06-29 中南大学 Special Al-Cr heat-resistant alloy powder for 3D printing, preparation method and application thereof, and Al-Cr heat-resistant alloy
CN113249668A (en) * 2021-04-30 2021-08-13 哈尔滨工程大学 Method for improving anisotropy of additive manufacturing titanium alloy by using pulse current
CN113512671A (en) * 2021-06-15 2021-10-19 中车工业研究院有限公司 High-toughness AlCrSc alloy powder for 3D printing and preparation method and application thereof
CN114507817A (en) * 2022-01-20 2022-05-17 上海材料研究所 Ultra-low carbon cobalt-free high-strength corrosion-resistant alloy and preparation method and application thereof

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101298653A (en) * 2008-05-26 2008-11-05 清华大学深圳研究生院 High-strength high-toughness AZ91 magnesium alloy strip eletrotoughening process method and system
CN102363215A (en) * 2011-11-04 2012-02-29 中南大学 Method for preparing chromium aluminum alloy target by powder vacuum hot pressed sintering
CN109290583A (en) * 2018-11-16 2019-02-01 华南理工大学 A method of it eliminating 7075 aluminium alloy selective laser meltings and forms crackle
US20190040503A1 (en) * 2017-08-03 2019-02-07 Hrl Laboratories, Llc Feedstocks for additive manufacturing, and methods of using the same
CN109844150A (en) * 2016-07-05 2019-06-04 纳诺尔有限责任公司 Band and powder from high-strength corrosion-resisting aluminium alloy
WO2019155165A1 (en) * 2018-02-08 2019-08-15 C-Tec Constellium Technology Center Process for manufacturing an aluminum-chromium alloy part

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101298653A (en) * 2008-05-26 2008-11-05 清华大学深圳研究生院 High-strength high-toughness AZ91 magnesium alloy strip eletrotoughening process method and system
CN102363215A (en) * 2011-11-04 2012-02-29 中南大学 Method for preparing chromium aluminum alloy target by powder vacuum hot pressed sintering
CN109844150A (en) * 2016-07-05 2019-06-04 纳诺尔有限责任公司 Band and powder from high-strength corrosion-resisting aluminium alloy
US20190040503A1 (en) * 2017-08-03 2019-02-07 Hrl Laboratories, Llc Feedstocks for additive manufacturing, and methods of using the same
WO2019155165A1 (en) * 2018-02-08 2019-08-15 C-Tec Constellium Technology Center Process for manufacturing an aluminum-chromium alloy part
CN109290583A (en) * 2018-11-16 2019-02-01 华南理工大学 A method of it eliminating 7075 aluminium alloy selective laser meltings and forms crackle

Cited By (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111531172A (en) * 2020-05-29 2020-08-14 同济大学 3D printing process method of high-strength aluminum-silicon alloy
CN112813310A (en) * 2020-06-28 2021-05-18 中南大学 High-strength Al-Fe-Sc alloy capable of being used for laser additive manufacturing
CN111659889A (en) * 2020-06-30 2020-09-15 同济大学 3D printing process method of high-strength aluminum-manganese alloy
CN111673085A (en) * 2020-06-30 2020-09-18 同济大学 3D printing process method of high-strength aluminum-magnesium-silicon alloy
CN112620649A (en) * 2020-11-30 2021-04-09 华中科技大学 Aluminum alloy material and laser 3D printing aluminum alloy component based on same
CN112620649B (en) * 2020-11-30 2022-04-12 华中科技大学 Aluminum alloy material and laser 3D printing aluminum alloy component based on same
CN113042729A (en) * 2021-03-16 2021-06-29 中南大学 Special Al-Cr heat-resistant alloy powder for 3D printing, preparation method and application thereof, and Al-Cr heat-resistant alloy
CN113042729B (en) * 2021-03-16 2022-05-06 中南大学 Special Al-Cr heat-resistant alloy powder for 3D printing, preparation method and application thereof, and Al-Cr heat-resistant alloy
CN113249668A (en) * 2021-04-30 2021-08-13 哈尔滨工程大学 Method for improving anisotropy of additive manufacturing titanium alloy by using pulse current
CN113249668B (en) * 2021-04-30 2022-05-20 哈尔滨工程大学 Method for improving anisotropy of additive manufacturing titanium alloy by using pulse current
CN113512671A (en) * 2021-06-15 2021-10-19 中车工业研究院有限公司 High-toughness AlCrSc alloy powder for 3D printing and preparation method and application thereof
CN114507817A (en) * 2022-01-20 2022-05-17 上海材料研究所 Ultra-low carbon cobalt-free high-strength corrosion-resistant alloy and preparation method and application thereof

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