CN117884649B - Laser additive manufacturing process of magnetostrictive material iron-gallium alloy - Google Patents
Laser additive manufacturing process of magnetostrictive material iron-gallium alloy Download PDFInfo
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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
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Abstract
The invention relates to the technical field of magnetic material and laser additive manufacturing, in particular to a laser additive manufacturing process of magnetostrictive material iron-gallium alloy. The manufacturing process comprises the following steps: in the laser additive manufacturing process, laser secondary exposure remelting is carried out in the same layer after laser scanning. The process adopts the additive manufacturing process, and compared with the traditional forming method, the integrated forming of the shape of the part is irrelevant, the process is green and environment-friendly, does not need complex process flow, and has high efficiency and high yield. According to the invention, the <100> orientation, the thermal cycle and the thermal accumulation process of the Fe-Ga alloy formed by laser additive are enhanced by regulating and controlling the technological parameters, so that the strong anisotropy is achieved, and the nano precipitated phase is regulated and controlled to improve the magnetostriction performance of the Fe-Ga alloy. The magnetostriction performance of the Fe-Ga (polycrystalline) alloy material prepared by the process is improved by 1-3 times compared with that of Fe-Ga alloy which is remelted by secondary exposure.
Description
Technical Field
The invention relates to the technical field of magnetic material and laser additive manufacturing, in particular to a laser additive manufacturing process of magnetostrictive material iron-gallium alloy.
Background
Magnetostrictive materials play an increasingly important role in modern industrial applications such as stress sensors, actuators, transducers, and the like. The Fe-Ga alloy has the excellent comprehensive properties of large magnetostriction coefficient, good mechanical property, low cost, high Curie temperature, good thermal stability, high magnetic conductivity and the like. The traditional iron-gallium alloy is mainly prepared around single crystals or polycrystal which can obtain orientation of easy magnetization direction <100>, such as directional solidification, quick quenching of melt-spun, rolling, magnetron sputtering and the like. Obviously, the iron-gallium alloy prepared by the traditional method is limited to simple blocks, strips or films in terms of shape and structure, and has great limitation in terms of size and three-dimensional structure. The additive manufacturing technology is suitable for the rapid research and development of new products with complex structures, inner cavity structures and other characteristics, can realize the integrated design and additive manufacturing forming of components, and saves a great amount of manufacturing period and cost; laser additive manufacturing technology is one of the most popular metal additive manufacturing technologies at present. Although the material manufactured by laser additive has anisotropy, the magnetostriction performance of the iron-gallium alloy in the prior art still needs to be further improved.
Disclosure of Invention
Based on the above, the invention provides a laser additive manufacturing process of a magnetostrictive material iron-gallium alloy, so as to improve the magnetostriction performance of the magnetostrictive material iron-gallium alloy.
In order to achieve the above object, the present invention provides the following solutions:
According to one of the technical schemes of the invention, in the manufacturing process of the magnetostrictive material iron-gallium alloy, laser secondary exposure remelting is carried out in the same layer after laser scanning in the manufacturing process of the laser additive.
Further, the iron-gallium alloy is Fe 1-xGax, x represents Ga atomic percent, x=15-30 at%.
Further, the method comprises the following steps:
carrying out laser scanning on the iron-gallium alloy powder, and then carrying out laser secondary exposure remelting in the same layer; repeating the steps of laser scanning and laser secondary exposure remelting to obtain the iron-gallium alloy.
Further, the technological parameters of the laser scanning are as follows: the diameter of the light spot is 50-100 mu m; the laser power is 100-500W; the laser scanning speed is 500-5000 mm/s; the scanning interval is 0.05-0.2 mm; the layer thickness is 30-50 μm; the laser scan angle is one of 0 °, 67 °, or 90 °.
Further, the laser power of the laser secondary exposure remelting is 60% -80% of the laser power of the laser scanning.
Further, the scanning speed of the laser secondary exposure remelting is 20% -60% of the scanning speed of the laser scanning; the scanning interval of the laser secondary exposure remelting is 30% -60% of the scanning interval of the laser scanning; the diameter of the light spot remelted by the laser secondary exposure is 50-100 mu m.
Further, the scanning angle of the laser secondary exposure remelting is 0 °.
According to the second technical scheme, the magnetostrictive material iron-gallium alloy is prepared by the laser additive manufacturing process of the magnetostrictive material iron-gallium alloy.
According to the third technical scheme, the magnetostrictive material iron-gallium alloy is applied to stress sensors, actuators or transducers.
According to the fourth technical scheme, the method for improving the magnetostriction performance of the iron-gallium alloy adopts the laser additive manufacturing process of the magnetostriction material iron-gallium alloy.
The invention discloses the following technical effects:
The method has simple and quick process, and can obtain the iron-gallium alloy (Fe-Ga alloy) with excellent magnetostriction performance without adopting complex process methods such as rolling, directional solidification, heat treatment and the like to enhance the tissue anisotropy.
The process disclosed by the invention adopts the characteristic of in-situ heat treatment in the additive manufacturing process, and is environment-friendly, free of complex process flow, high in efficiency and high in yield compared with the traditional forming method regardless of the shape of the part.
According to the invention, the thermal cycle and the heat accumulation process of the formed Fe-Ga alloy are changed by regulating and controlling the technological parameters, and the nano precipitated phase is regulated and controlled to improve the magnetostriction performance of the Fe-Ga alloy. The magnetostriction performance of the Fe-Ga (polycrystalline) alloy material prepared by the process is improved by 1-3 times compared with that of Fe-Ga alloy which is remelted by secondary exposure.
Drawings
In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the drawings that are needed in the embodiments will be briefly described below, and it is obvious that the drawings in the following description are only some embodiments of the present invention, and other drawings may be obtained according to these drawings without inventive effort for a person skilled in the art.
FIG. 1 is a graph showing particle size distribution and morphology of Fe81Ga19 alloy powder in example 1 of the present invention; wherein (a) is particle size distribution and (b) is a topography.
FIG. 2 is a microstructure micrograph of the Fe81Ga19 alloy of example 1 of the present invention at 500 Xmagnification by laser remelting.
FIG. 3 shows magnetostriction curves of the Fe81Ga19 alloy additive manufactured by laser remelting and unmelting at different laser powers in comparative example 1 and comparative example 2 according to the present invention.
FIG. 4 is a scanning electron micrograph of a microstructure of an Fe81Ga19 alloy according to comparative example 1 of the present invention, which has not been subjected to laser remelting; wherein, (a) is a scanning electron micrograph at 1000 times magnification, (b) is a scanning electron micrograph at 4000 times magnification, (c) is a scanning electron micrograph at 4500 times magnification, and (d) is a scanning electron micrograph at 10000 times magnification.
FIG. 5 is a pole diagram along the construction direction of the Fe81Ga19 alloy prepared in example 1, comparative example 1 and comparative example 2 of the present invention; wherein (a) is example 1, (b) is comparative example 1, and (c) is comparative example 2.
Detailed Description
Various exemplary embodiments of the invention will now be described in detail, which should not be considered as limiting the invention, but rather as more detailed descriptions of certain aspects, features and embodiments of the invention.
It is to be understood that the terminology used herein is for the purpose of describing particular embodiments only and is not intended to be limiting of the invention. In addition, for numerical ranges in this disclosure, it is understood that each intermediate value between the upper and lower limits of the ranges is also specifically disclosed. Every smaller range between any stated value or stated range, and any other stated value or intermediate value within the stated range, is also encompassed within the invention. The upper and lower limits of these smaller ranges may independently be included or excluded in the range.
Unless otherwise defined, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs. Although only preferred methods and materials are described herein, any methods and materials similar or equivalent to those described herein can be used in the practice or testing of the present invention. All documents mentioned in this specification are incorporated by reference for the purpose of disclosing and describing the methods and/or materials associated with the documents. In case of conflict with any incorporated document, the present specification will control.
It will be apparent to those skilled in the art that various modifications and variations can be made in the specific embodiments of the invention described herein without departing from the scope or spirit of the invention. Other embodiments will be apparent to those skilled in the art from consideration of the specification of the present invention. The specification and examples of the present invention are exemplary only.
As used herein, the terms "comprising," "including," "having," "containing," and the like are intended to be inclusive and mean an inclusion, but not limited to.
The first aspect of the invention provides a laser additive manufacturing process of magnetostrictive material iron-gallium alloy, wherein laser secondary exposure remelting is carried out in the same layer after laser scanning in the laser additive manufacturing process.
The Fe-Ga alloy is of a body-centered cubic structure, has obvious magnetostriction anisotropy, and is specifically expressed as follows: there is a maximum magnetostriction coefficient along the <100> direction. The uniform and shallow small melt pool generated at the top position of each layer inhibits the lateral (horizontal) growth of crystal grains from the side surface of the initial (main) melt pool through laser secondary exposure remelting, enhances the epitaxial growth of crystal grains along the construction direction and generates the action of directional solidification. Meanwhile, magnetostriction of the Fe-Ga alloy is also related to precipitation of nano tetragonal precipitation L60 phase. The precipitation of the L60 phase is highly related to the thermal history of the material, and the magnetostriction performance can be highest when the size and the number density of the L60 phase are regulated to be within a specific range through a proper heat treatment process. The unique process characteristics of cyclic heating, rapid cooling and high temperature gradient of the additive manufacturing technology enable the forming process to be in a complex temperature field, stress field and fluid field, and the thermal history in the forming process of the iron-gallium alloy can be changed by changing additive manufacturing parameters, so that the effect of customizing microstructure is achieved, and the magnetostriction performance of the iron-gallium alloy is improved.
In the invention, the first laser scanning is used for melting powder and forming materials, the second remelting is used for generating a remelting layer on the surface of a formed block, the remelting layer molten pool has the characteristic of being flat, a large number of columnar crystals growing in the super-construction direction are generated in the molten pool, and externally-derived growth nucleation sites are provided for the next laser scanning, so that the anisotropy of the materials is increased. Meanwhile, the heating cycle and heat accumulation are increased, and the precipitation of nano precipitation phases is increased, so that the magnetostriction performance of the iron-gallium alloy is improved.
In a preferred embodiment of the invention, the iron-gallium alloy is Fe 1-xGax, x represents Ga atomic percent, x=15-30 at%. Further preferably, the iron-gallium alloy is Fe81Ga19.
In a preferred embodiment of the invention, the method comprises the steps of:
carrying out laser scanning on the iron-gallium alloy powder, and then carrying out laser secondary exposure remelting in the same layer; repeating the steps of laser scanning and laser secondary exposure remelting to obtain the iron-gallium alloy.
In a preferred embodiment of the present invention, the process parameters of the laser scanning are: the diameter of the light spot is 50-100 mu m; the laser power is 100-500W; the laser scanning speed is 500-5000 mm/s; the scanning interval is 0.05-0.2 mm; the layer thickness is 30-50 μm; the laser scan angle is one of 0 °, 67 °, or 90 °. A further preferred laser scan angle is 90 °.
In a preferred embodiment of the invention, the laser energy of the laser secondary exposure remelting is lower than the laser energy of the laser scanning; specifically, the laser power of the laser secondary exposure remelting is 60% -80% of the laser power of the laser scanning.
In a preferred embodiment of the invention, the scanning speed of the laser secondary exposure remelting is 20% -60% of the scanning speed of the laser scanning; the scanning interval of the laser secondary exposure remelting is 30% -60% of the scanning interval of the laser scanning; the diameter of the light spot remelted by the laser secondary exposure is 50-100 mu m.
In a preferred embodiment of the present invention, the laser secondary exposure reflow scan angle is 0 °.
According to the invention, through the optimized technological parameters and the special technological process, the iron-gallium alloy with excellent magnetostriction performance can be prepared. When the laser forming process parameters are not in the protection scope of the invention, the magnetostriction performance of the alloy can be greatly reduced. If the laser power of laser secondary exposure remelting is smaller than or the scanning speed of laser secondary exposure remelting is larger than or the scanning interval of laser secondary exposure remelting is larger than the range defined by the invention, the remelting melting channel can be completely covered by the next scanning due to low energy and small melting depth, and the effect of enhancing the anisotropy cannot be achieved. On the contrary, when the laser power of the laser secondary exposure remelting is larger or the scanning speed of the laser secondary exposure remelting is smaller or the scanning interval of the laser secondary exposure remelting is smaller than the range defined by the invention, the epitaxial growth is weakened due to high energy and large melting depth, so that the anisotropy is not enhanced, the heat accumulation is increased, and the magnetostriction performance is greatly reduced.
The laser secondary exposure remelting is carried out in the same layer, and the reason that the laser energy of the laser secondary exposure remelting is lower than that of the laser scanning is as follows: the remelting is carried out by adopting low-energy laser, so that a uniform and shallow small molten pool can be generated at the top position of each layer, the transverse (horizontal) growth of crystal grains from the side surface of the initial (main) molten pool can be restrained, the epitaxial growth of the crystal grains along the construction direction is enhanced, and the directional solidification effect is generated. The additional heat input of the low energy laser secondary exposure reflow sweep results in a more uniform solidification pattern that allows thermal cycling and heat accumulation experienced by the shaped portion to meet the nanophase precipitation conditions.
The reason why the scanning angle of the laser secondary exposure reflow is defined as 0 ° is that: the laser secondary exposure remelting is the same as the laser path direction of laser scanning, so that the transverse (horizontal) growth of crystal grains from the side surface of the initial (main) molten pool can be effectively inhibited, the epitaxial growth of the crystal grains is increased, and the anisotropism is enhanced.
In some embodiments of the present invention, a laser additive manufacturing process of an iron-gallium alloy comprises the steps of:
S1, drying special Fe-Ga alloy powder for additive manufacturing in a vacuum environment;
S2, adding the dried Fe-Ga alloy powder into a printer powder bin, introducing inert gas argon as a protective atmosphere, and starting printing when the oxygen content in the bin is reduced to below 80 ppm;
S3, paving Fe-Ga alloy powder to form a powder layer; carrying out laser scanning on the powder layer by adopting optimized process parameters;
S4, performing laser secondary exposure remelting by adopting laser power, scanning speed and scanning interval and scanning angle of 0 DEG which are lower than those in the process parameters optimized in the S3;
s5, sequentially circulating the S3-S4 to form a complete Fe-Ga alloy sample;
s6, after the sample is separated from the substrate, testing the magnetostriction coefficient of the sample.
In some embodiments of the present invention, in step S1, the drying under vacuum environment is: and drying the materials in a vacuum environment at 60-120 ℃ for 4-12 h.
In some embodiments of the present invention, in step S3, the powder layer is scanned by using optimized process parameters, where a spot diameter of the laser scanning is 50-100 μm, and a scanning path is scanned in parallel and reciprocally.
In some embodiments of the present invention, in step S3, the optimized process parameters are: the laser power is 100-500W, the laser scanning speed is 500-5000 mm/s, the scanning interval of laser is 0.05-0.2 mm, the powder spreading thickness is 30-50 μm, the interlayer rotation angle is any one of 0 degree, 67 degree and 90 degree, wherein 90 degree is preferable.
In some embodiments of the present invention, in step S4, the parameters of the laser secondary exposure reflow are: the laser power is 10-200W, the laser scanning speed is 100-5000 mm/s, the scanning interval of the laser is 0.01-0.2 mm, and the laser rotation angle is 0 degrees.
In some embodiments of the present invention, after the part is separated from the substrate in step S6, the magnetostriction coefficient of the part is tested, the magnetostriction measurement method is a strain gauge method, the sample size is 12×10×3mm, and the length direction of 12 mm is the direction of easy magnetization.
The second aspect of the invention provides the magnetostrictive material iron-gallium alloy prepared by the laser additive manufacturing process of the magnetostrictive material iron-gallium alloy.
A third aspect of the invention provides the use of a magnetostrictive material iron-gallium alloy as described above in a stress sensor, actuator or transducer.
The fourth aspect of the invention provides a method for improving magnetostriction performance of an iron-gallium alloy, which adopts the laser additive manufacturing process of the magnetostriction material iron-gallium alloy.
The raw materials used in the examples of the present invention, unless otherwise specified, are all available commercially.
The invention is further illustrated by the following examples.
Example 1: a laser additive manufacturing process for preparing high magnetostriction performance iron-gallium alloy comprises the following steps:
S1, before additive manufacturing, drying Fe81Ga19 alloy powder in a vacuum drying oven at 70 ℃ for 10 hours to remove water; wherein the particle size distribution of the Fe81Ga19 alloy powder is 15-53 mu m, and the morphology and the particle size distribution are shown in figure 1;
S2, adopting a 316L stainless steel substrate with the size of 100 multiplied by 23 mm 3, polishing the surface of the substrate with sand paper to be smooth, and cleaning with alcohol; a powder bed fusion apparatus of a HANS-M-100 laser equipped with a fiber laser having a spot diameter of 0.05 mm was used to produce a bulk sample of Fe81Ga 19. In order to prevent oxidation, argon is used as a protective atmosphere, and the oxygen content in the molding bin is controlled below 100 ppm;
S3, modeling of a 10 mm multiplied by 10 multiplied by mm multiplied by 30 mm block sample is completed by using Magics software, and the process parameters are set as follows: the diameter of the light spot is 0.05mm, the laser power P is 120W, the scanning speed V is 1100 mm/s, the scanning interval is 0.06 mm, the layer thickness is 0.04 mm, and the interlayer rotation angle is 90 degrees;
S4, performing laser secondary exposure in the same layer, wherein each layer is repeated, the laser power of laser secondary exposure remelting is 80W, the scanning speed is 500 mm/s, the scanning interval is 0.03 mm, and the scanning angle is 0 degree; forming a complete Fe81Ga19 block sample;
s5, cutting and separating the block sample from the substrate by adopting a linear cutting mode; taking a 12 mm multiplied by 10mm multiplied by 3 mm sample, polishing the surface to be smooth by sand paper, cleaning the surface by acetone, drying, adhering a BX120-3AA strain gauge with the model number of BX120-3AA to the 12 mm multiplied by 10mm surface of the sample by 502 glue, and enabling the easy magnetization direction to be along the length direction of 12 mm; testing magnetostriction coefficient lambda parallel to the magnetic field direction by using a model JDAW-2015 magnetostriction measurement system; in order to observe the structure morphology and the precipitated phase of the Fe81Ga19 alloy in the additive manufacturing, metallographic sand papers of #120, #400, #800, #1200, #2500 and #5000 are sequentially adopted to grind and polish the surface of a sample, 10% nitric acid alcohol solution is adopted for corrosion, and an optical microscope and a field emission scanning electron microscope are adopted to observe and analyze the appearance of a molten pool and the precipitated phase precipitation condition.
The magnetostriction performance λ of the additive manufactured Fe81Ga19 alloy prepared in example 1 is 80 ppm; the microstructure is shown in fig. 2, remelting layer and initial scanning layer structure are generated by laser secondary exposure remelting in the same layer, the remelting layer has the characteristic of a flat molten pool, the <100> orientation is enhanced, and as shown in (a) in fig. 5, a sample remelted by secondary exposure has a cubic {001} <100> texture, and the strength is greater than 10, so that the magnetostriction performance of the sample is greatly improved.
Comparative example 1
The difference from example 1 is that step S4 (laser secondary exposure reflow in the same layer) is omitted, and the other steps and parameters are the same as in example 1.
In contrast to example 1, no laser secondary exposure reflow was performed in the printing parameters of comparative example 1, with a single scan in the layer; the magnetostriction performance λ of the additive manufactured Fe81Ga19 alloy in comparative example 1 was 37 ppm, and the magnetostriction contrast curve is shown in fig. 3 (in fig. 3, laser remelting represents example 1, and no laser remelting represents comparative example 1); the microstructure of the Fe81Ga19 alloy additively produced in comparative example 1 is shown in fig. 4, and it can be seen from fig. 4 that the Fe81Ga19 alloy produced by laser additive production (without laser secondary exposure remelting) of comparative example 1 is enlarged to different multiples, and no significant precipitated phase appears inside. As shown in fig. 5, comparing the presence or absence of remelting the polar diagram by laser secondary exposure (i.e., fig. 5 (a), (b)), the specimens remelted by secondary exposure had a cubic {001} <100> texture and the intensity was greater than 10. The magnetostriction performance was less than 1/2 of that of example 1.
Comparative example 2
The difference from example 1 is that the laser secondary exposure remelting laser power in step S4 is 50W, and the other steps and parameters are the same as those in example 1.
In comparison with example 1, the laser power of laser secondary exposure remelting in the printing parameters in comparative example 2 is 40% of the initial scanning laser power, the magnetostriction performance λ of the additive manufactured Fe81Ga19 alloy in comparative example 2 is 40 ppm, and the magnetostriction contrast curve is shown in fig. 3 (in fig. 3, 80W laser remelting represents example 1, no laser remelting represents comparative example 1, and 50W laser remelting represents comparative example 2); as shown in FIG. 5 (c), the polar diagram of the Fe81Ga19 alloy for the additive manufacturing in comparative example 2 shows that the sample remelted by 50W double exposure has a cubic {001} <100> texture, but has a maximum strength of only 4.39 and magnetostriction performance of about 1/2 of that of example 1.
The above embodiments are only illustrative of the preferred embodiments of the present invention and are not intended to limit the scope of the present invention, and various modifications and improvements made by those skilled in the art to the technical solutions of the present invention should fall within the protection scope defined by the claims of the present invention without departing from the design spirit of the present invention.
Claims (5)
1. The laser additive manufacturing process of the magnetostrictive material iron-gallium alloy is characterized by comprising the following steps of:
carrying out laser scanning on the iron-gallium alloy powder, and then carrying out laser secondary exposure remelting in the same layer; repeating the steps of laser scanning and laser secondary exposure remelting to obtain the iron-gallium alloy;
the scanning angle of the laser secondary exposure remelting is 0 degree;
The laser power of the laser secondary exposure remelting is 60% -80% of the laser power of the laser scanning;
The technological parameters of the laser scanning are as follows: the diameter of the light spot is 50-100 mu m; the laser power is 100-500W; the laser scanning speed is 500-5000 mm/s; the scanning interval is 0.05-0.2 mm; the layer thickness is 30-50 μm; the laser scanning angle is one of 0 DEG, 67 DEG or 90 DEG;
the scanning speed of the laser secondary exposure remelting is 20% -60% of the scanning speed of the laser scanning;
The scanning interval of the laser secondary exposure remelting is 30% -60% of the scanning interval of the laser scanning.
2. The laser additive manufacturing process of a magnetostrictive material iron-gallium alloy according to claim 1, wherein the iron-gallium alloy is Fe 1-xGax, x represents Ga atomic percent, x = 15-30 at%.
3. The process for laser additive manufacturing of magnetostrictive material iron-gallium alloy according to claim 1, wherein the spot diameter of the laser secondary exposure remelting is 50-100 μm.
4. A magnetostrictive material iron-gallium alloy prepared by a laser additive manufacturing process of the magnetostrictive material iron-gallium alloy according to any one of claims 1-3.
5. Use of a magnetostrictive material iron-gallium alloy according to claim 4 in a stress sensor, an actuator or a transducer.
Priority Applications (1)
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| CN109487152A (en) * | 2019-01-11 | 2019-03-19 | 中南大学 | A kind of cell stimulating activity and magnetostriction iron-gallium alloy of fast degradation and preparation method thereof |
| CN115703153A (en) * | 2021-08-17 | 2023-02-17 | 中国科学院福建物质结构研究所 | Method for optimizing nickel-titanium alloy performance based on selective laser melting method |
| CN115889808A (en) * | 2022-10-20 | 2023-04-04 | 成都先进金属材料产业技术研究院股份有限公司 | Selective laser melting molding high-temperature alloy and production method thereof |
| CN116251965A (en) * | 2023-02-28 | 2023-06-13 | 西北工业大学 | Method for improving magnetic performance of neodymium-iron-boron alloy manufactured by laser additive |
| CN117157160A (en) * | 2021-04-13 | 2023-12-01 | 国立大学法人东北大学 | Method for producing magnetostrictive material, and method for producing energy conversion member |
| CN117431451A (en) * | 2023-10-30 | 2024-01-23 | 中南大学 | Method for preparing magnetostrictive Fe-Ga alloy by laser powder bed melting and magnetic field annealing |
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| EP2865465B1 (en) * | 2013-09-27 | 2018-01-17 | Ansaldo Energia IP UK Limited | Method for manufacturing a metallic component by additive laser manufacturing |
| PL415814A1 (en) * | 2016-01-15 | 2017-07-17 | Politechnika Warszawska | Method for additive production of three-dimensional objects from metallic glass |
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| CN109487152A (en) * | 2019-01-11 | 2019-03-19 | 中南大学 | A kind of cell stimulating activity and magnetostriction iron-gallium alloy of fast degradation and preparation method thereof |
| CN117157160A (en) * | 2021-04-13 | 2023-12-01 | 国立大学法人东北大学 | Method for producing magnetostrictive material, and method for producing energy conversion member |
| CN115703153A (en) * | 2021-08-17 | 2023-02-17 | 中国科学院福建物质结构研究所 | Method for optimizing nickel-titanium alloy performance based on selective laser melting method |
| CN115889808A (en) * | 2022-10-20 | 2023-04-04 | 成都先进金属材料产业技术研究院股份有限公司 | Selective laser melting molding high-temperature alloy and production method thereof |
| CN116251965A (en) * | 2023-02-28 | 2023-06-13 | 西北工业大学 | Method for improving magnetic performance of neodymium-iron-boron alloy manufactured by laser additive |
| CN117431451A (en) * | 2023-10-30 | 2024-01-23 | 中南大学 | Method for preparing magnetostrictive Fe-Ga alloy by laser powder bed melting and magnetic field annealing |
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