CN111842888A - 4D printing method of nickel titanium based ternary shape memory alloy - Google Patents
4D printing method of nickel titanium based ternary shape memory alloy Download PDFInfo
- Publication number
- CN111842888A CN111842888A CN202010562592.1A CN202010562592A CN111842888A CN 111842888 A CN111842888 A CN 111842888A CN 202010562592 A CN202010562592 A CN 202010562592A CN 111842888 A CN111842888 A CN 111842888A
- Authority
- CN
- China
- Prior art keywords
- printing
- shape memory
- memory alloy
- ternary
- alloy
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
Images
Classifications
-
- 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
-
- 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
- B33Y70/00—Materials specially adapted for 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
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/0433—Nickel- or cobalt-based 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
- C22C1/047—Making non-ferrous alloys by powder metallurgy comprising intermetallic compounds
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Powder Metallurgy (AREA)
Abstract
The invention belongs to the technical field of 4D printing additive manufacturing, and discloses a 4D printing method of a nickel titanium based ternary shape memory alloy, which is characterized in that the method adopts a laser selective melting technology to print gas atomization prefabricated NiTiZr ternary alloy powder, and a component obtained by printing has a shape memory function; the laser energy density is changed by changing the technological parameters adopted by the selective laser melting technology, so that the change of the organization and the performance of the printed piece is regulated and controlled. According to the invention, the third component Zr is introduced into the existing nickel-titanium binary alloy, so that the martensite phase transition temperature is obviously increased, and the forming is realized by adopting a selective laser melting technology, so that the excellent shape memory property and mechanical property are ensured, and the complex parts with uniform tissues and high density are favorably obtained.
Description
Technical Field
The invention belongs to the technical field of 4D printing additive manufacturing, and particularly relates to a 4D printing method of a nickel titanium based ternary shape memory alloy, which is a material additive manufacturing method of a NiTiZr ternary shape memory alloy.
Background
The 4D printing belongs to an additive manufacturing technology, intelligent materials with excitation response can be introduced, the intelligent materials are formed through the additive manufacturing technology, the static state of the traditional 3D printing is broken, the self-assembling, self-sensing and self-adapting performances are improved, and a new development opportunity is brought to the manufacturing of high-end intelligent components.
As an important shape memory alloy intelligent material, the NiTi alloy is widely applied to the fields of aerospace, automobiles, biomedical treatment, petroleum and the like due to the advantages of excellent shape memory effect, superelasticity, high damping property, corrosion resistance, biocompatibility and the like. However, the transformation temperature of the nickel-titanium binary alloy is low and is not more than 100 ℃, so that the application of the nickel-titanium binary alloy in high-temperature occasions is limited. In recent years, the research finds that the addition of elements can change the phase transition temperature range of the NiTi alloy and improve the stability and the memory performance of the material. The NiTiZr ternary alloy obtained by using Zr to replace Ti can obviously improve the martensite phase transition temperature of the NiTi alloy, and has important significance for widening the application range of the NiTi alloy, researching functional gradient manufacturing and composite manufacturing.
In addition, due to the phenomena of rebound effect, work hardening, burrs and the like in the NiTi-based alloy machining process, the traditional cold machining method cannot meet the part manufacturing requirements easily. The traditional high-temperature processing method (such as smelting, casting and the like) has the problems of increased impurity content, oxidized inclusion and the like, thereby influencing the shape memory effect. The prior research successfully solidifies the NiTiZi thin strip by a plane flow casting technology, prepares a NiTiZi film by sputtering deposition and prepares a NiTiZi block by equal channel angular extrusion. However, the preparation method has a single shape and low forming precision, and is difficult to meet the manufacturing requirement of the complex structure of the 4D printing component.
Disclosure of Invention
Aiming at the defects or improvement requirements of the prior art, the invention aims to provide a 4D printing method of a nickel titanium based ternary shape memory alloy, which obviously improves the martensite phase transition temperature by introducing a third component Zr into the prior nickel titanium binary alloy, adopts a selective laser melting technology for forming, ensures excellent shape memory performance and mechanical performance, and is beneficial to obtaining complex parts with uniform tissues and high density. The invention can obtain the NiTiZr shape memory alloy part by utilizing the selective laser melting technology for the first time, and obtains the printing parts with different laser energy densities by changing the laser process parameters, thereby changing the mechanical property, the organization, the shape memory property and the phase transition temperature of the printing parts.
In order to achieve the purpose, the invention provides a 4D printing method of a nickel titanium based ternary shape memory alloy, which is characterized in that the method adopts a laser selective melting technology to print gas atomization prefabricated NiTiZr ternary alloy powder, and a printed component has a shape memory function; the laser energy density is changed by changing the technological parameters adopted by the selective laser melting technology, so that the change of the organization and the performance of the printed piece is regulated and controlled.
In a further preferred embodiment of the present invention, the NiTiZr ternary alloy powder is Ti having a particle size of 15 to 53 μm42.5Ni49.5Zr8The powder preferably has an average particle size of 33 μm.
As a further optimization of the invention, a laser scanning strategy adopted by the selective laser melting technology is strip partition and interlayer rotation, wherein the partition width is 4-10 mm, and the interlayer rotation angle is 16-67 degrees.
In a further preferred embodiment of the present invention, the partition width is 10mm, and the interlayer rotation angle is 16 °.
As a further preferred embodiment of the present invention, the printing parameters adopted by the selective laser melting technology are set as follows: the laser power is 160-280W, the scanning speed is 700-1300 mm/s, the scanning interval is 0.12mm, the powder spreading layer thickness is 0.03mm, and the substrate preheating temperature is 200 ℃.
As a further preferred aspect of the present invention, the process parameters adopted by the selective laser melting technique are set as follows: the laser power is 250W, the scanning speed is 1000mm/s, and the laser energy density is 69.44J/mm3。
As a further preferred mode of the invention, the technological parameters adopted by the selective laser melting technology are required to ensure that the laser energy density is more than 34.19J/mm3。
As a further optimization of the invention, in the printing process adopting the selective laser melting technology, the oxygen content of the equipment is less than or equal to 500ppm, argon is introduced as protective gas, and the gas pressure is kept at 10-20 mbar.
As a further preferred aspect of the present invention, the maximum density of the printed member is 6.537g/cm3The maximum hardness is 5.3Gpa, and the martensite phase transformation peak temperature range is 91-104 ℃.
As a further preferred aspect of the present invention, the printed member has a phase composition including a (Ti, Zr) Ni phase, a ternary mesophase λ 1, and a monoclinic martensite phase B19'.
Through the above technical scheme, compared with the prior art, the NiTiZr ternary alloy is used for additive manufacturing, the additive manufacturing technology adopts a laser selective melting manufacturing process, the NiTiZr shape memory alloy member formed based on the method has a shape memory effect, and martensite positive phase transformation and reverse phase transformation exist in the cooling and heating processes; the maximum hardness of the formed NiTiZr shape memory alloy part is 5.3Gpa, the martensite phase transformation peak temperature range is 91-104 ℃, and the temperature is 30-70 ℃ higher than the transformation peak temperature of nickel-titanium binary alloy researched and developed by the literature.
Specifically, the present invention can achieve the following advantageous effects:
1. in the invention, Zr element is introduced into the NiTi alloy, so that the phase transition temperature is obviously improved, the phase stability is increased, the material cost is relatively low, and the adaptability is strong. The invention can especially select 8% Zr content, which will not affect the plasticity, tensile strain and other mechanical properties of the alloy because of too much Zr content, and will not change the martensitic transformation temperature obviously because of too little Zr content. Lays a foundation for the future research of NiTi-NiTiZr composite material printing. The invention particularly adopts the NiTiZr ternary alloy powder prefabricated by gas atomization, compared with the alloy powder mixed mechanically, the components of the powder prefabricated by gas atomization are more uniform, and when the invention is applied, the structural components of the component can be prevented from being non-uniform, so that the invention is more suitable for the 4D printing process.
The invention combines the NiTiZr ternary memory alloy and the selective laser melting for 4D printing for the first time, can change the laser energy density by changing the technological parameters adopted by the selective laser melting technology, and regulate and control the change of the structure and the performance of a printed piece, and has obvious advantages compared with other application methods of the NiTiZr ternary alloy in the prior art.
2. The laser selective melting technology adopted by the invention is one of the mature technologies for metal additive manufacturing at present, the manufacturing is carried out by adopting a layer-by-layer accumulation method, the forming efficiency is high, the heat affected zone is small, the complex component with high density, uniform tissue and controllable microstructure can be processed, and the method is suitable for 4D printing manufacturing of memory alloy materials. Compared with the processes of vacuum induction melting, casting and the like, the method has more manufacturing flexibility and is not easy to introduce impurities such as oxygen, carbon and the like; compared with the conventional sintering method, the self-propagating high-temperature synthesis method and other processes, the method shortens the manufacturing period and has more uniform components; compared with the processes of hot isostatic pressing, magnetron sputtering and the like, the forming of parts with complex shapes can be completed, and the controllability of microstructures and local structures is realized.
3. The invention adopts a selective laser melting process, the preferred technological parameter is laser power of 160-280W, the scanning speed is 700-1300 mm/s, and the change of the components, the structure and the performance of a formed part is regulated and controlled by changing the technological parameter of the laser, so that the use requirements of different occasions are met. The attempt of the selective laser melting technology on the ternary shape memory alloy also provides a new idea for the manufacturing and research of the gradient nickel-titanium-based memory alloy.
4. The Ni-Ti based shape memory alloy powder used in the present invention may especially be an aerosolized prealloyed powder, as compared to a machineThe powder mixing mode has more uniform components. And through the printing comparison of different laser energy densities, the optimal process parameter combination is preferably selected, the laser power is 250W, the scanning speed is 1000mm/s, and the laser energy density is 69.44J/mm3And a forming scheme with smaller surface roughness and higher density is obtained.
In conclusion, the 4D printing method of the nickel titanium based shape memory alloy provided by the invention can obviously improve the martensite phase transition temperature, and is beneficial to obtaining high-density complex parts while ensuring excellent shape memory performance and mechanical property. The method can achieve the purpose of increasing the transformation temperature of the NiTi shape memory alloy, and the transformation temperature of the prepared NiTiZr shape memory alloy manufactured by the additive can reach 91-104 ℃.
Drawings
Fig. 1 is a printing mode of selective laser melting arranged according to the present invention.
In FIG. 2, (a), (b), (c), (d) are DSC curves of SLM-printed NiTiZr alloy examples 1 to 4, respectively, of the present invention. The characteristic temperature points of the martensitic transformation and the martensitic reverse transformation are marked in the figure.
FIG. 3 is an XRD plot of SLM-printed NiTiZr alloys of this invention, examples 1 to 4.
FIG. 4 is a microstructure view of example 1 of the present invention observed by electron microscopy.
FIG. 5 is a hardness value plot of SLM-printed NiTiZr alloy examples 1 through 4 of the present invention.
Detailed Description
In order to make the objects, technical solutions and advantages of the present invention more apparent, the present invention is described in further detail below with reference to the accompanying drawings and embodiments. It should be understood that the specific embodiments described herein are merely illustrative of the invention and are not intended to limit the invention. In addition, the technical features involved in the embodiments of the present invention described below may be combined with each other as long as they do not conflict with each other.
In general, the present invention provides a method for additive manufacturing of a NiTiZr shape memory alloy, comprising the steps of:
powder treatment: and (3) sieving the NiTiZr alloy powder prepared by gas atomization through a 200-mesh sieve, removing large-particle powder, and then putting the NiTiZr alloy powder into a vacuum drying oven to dry for more than 4 hours at 80 ℃ for later use.
Print setting: a10 mm × 10mm × 5mm block part is drawn by using three-dimensional modeling software and subjected to slicing processing, a partition printing mode can be set according to a printing path shown in FIG. 1, and a set engineering document can be copied into SLM printing equipment. The selected substrate material for printing is nickel-titanium alloy, the preheating temperature of the nickel-titanium substrate is set to be 200 ℃, powder spreading is started after vacuumizing, and the printing can be started after the powder spreading is observed to be smooth and good in flowability. In addition, the substrate is subjected to sand blasting treatment, so that powder spreading is facilitated.
The printing process comprises the following steps: the equipment starts scanning and printing according to the computer slicing data, when the manufacturing of one layer is finished, the workbench descends one layer thickness (the set layer thickness is 0.03mm), the powder spreading roller wheel spreads the powder again, the next layer manufacturing is carried out, and the processes are continuously circulated until the printing of the whole part is finished. And after the equipment is cooled and depressurized, removing the residual powder after the substrate with the printed piece is taken down, and cutting off the part by using linear cutting equipment. During printing, the oxygen content of the equipment is ensured to be less than or equal to 500ppm, argon is introduced as protective gas, and the air pressure is kept at 10-20 mbar.
Surface treatment: and (3) processing the surface of the part by using sand paper or an automatic grinding machine, and grinding away oxide scales formed by linear cutting to obtain the part with a smooth and bright surface.
The specific embodiment is as follows:
example 1
The parameters of the selective laser melting manufacturing process are as follows: laser power 160W, scanning speed 700 mm/s. The scanning pitch and the powder coating thickness were the same as in the other examples, and were 0.12mm and 0.03mm, respectively. The final calculated energy density was 63.94J/mm3。
Example 2
The parameters of the selective laser melting manufacturing process are as follows: the laser power was 250W and the scanning speed was 1000 mm/s. The scanning pitch and the powder coating thickness were the same as in the other examples, and were 0.12mm and 0.03mm, respectively. The final calculated energy density was 69.44J/mm 3。
Example 3
The parameters of the selective laser melting manufacturing process are as follows: laser power 280W, scanning speed 1000 mm/s. The scanning pitch and the powder coating thickness were the same as in the other examples, and were 0.12mm and 0.03mm, respectively. The final calculated energy density was 77.78J/mm3。
Example 4
The parameters of the selective laser melting manufacturing process are as follows: laser power 280W, scanning speed 700 mm/s. The scanning pitch and the powder coating thickness were the same as in the other examples, and were 0.12mm and 0.03mm, respectively. The final calculated energy density was 111.11J/mm3。
Table 1 below shows a comparison table of the key process parameters used in examples 1 to 4.
TABLE 1
Fig. 2 shows DSC curves for four examples. The martensitic transformation and the martensitic reverse transformation processes for the four examples are unimodal, indicating that only the transformation between the austenite B2 phase and the monoclinic martensite B19' phase occurs during the thermal cycle, with no R-phase transformation. And the peak temperature of the martensitic transformation is around 100 deg..
Figure 3 shows XRD curves for four examples. By comparison with the standard comparison card, the phase compositions were considered to be mainly (Ti, Zr) Ni (i.e., B2 parent phase), ternary mesophase λ 1, monoclinic martensite phase B19'. The B2 parent phase is a tetragonal system, so that the alloy can show super elasticity; the intermediate phase lambda 1 is a ternary solid solution and is a Laves phase with an MgZn2 structure. The phases of the four examples are substantially identical in composition and vary in content.
FIG. 4 is an electron micrograph of example 1, showing that the structure formed is continuous and uniform and the forming quality is good due to the high cooling rate.
Figure 5 shows the nanoindentation hardness values for four examples. As can be seen, as the laser energy density increases, the hardness of the printed material increases first and then decreases. The highest nano indentation hardness value can reach 5.3 Gpa.
Example 5
Laser selection areaThe melting manufacturing process parameters were as follows: laser power 160W and scanning speed 1300 mm/s. The scanning pitch and the powder coating thickness were the same as in the other examples, and were 0.12mm and 0.03mm, respectively. The final calculated energy density was 34.19J/mm3. Because the laser energy density is too low, the powder is not completely melted, the bonding among particles is not firm, and the phenomena of macrocracks, peeling off of the skin and the like occur, the obtained component can not be applied to occasions with high requirements on the component.
The ternary alloy powder raw materials adopted in the above examples are all prealloyed Ti prepared by adopting an air atomization mode42.5Ni49.5Zr8Powder, actually measured, the Ti content was 35.8 wt%, the Zr content was 12.51 wt%, and the balance was Ni. The particle size of the alloy powder is distributed between 13 and 53 mu m, and the average particle size of the powder is 33.0 mu m. Of course, the above embodiments are merely examples, and the present invention is also applicable to Ti-Ni-Zr ternary alloys of other compositional ratios.
It will be understood by those skilled in the art that the foregoing is only a preferred embodiment of the present invention, and is not intended to limit the invention, and that any modification, equivalent replacement, or improvement made within the spirit and principle of the present invention should be included in the scope of the present invention.
Claims (10)
1. A4D printing method of nickel titanium base ternary shape memory alloy is characterized in that the method is to print gas atomization prefabricated NiTiZr ternary alloy powder by adopting a laser selective melting technology, and a component obtained by printing has a shape memory function; the laser energy density is changed by changing the technological parameters adopted by the selective laser melting technology, so that the change of the organization and the performance of the printed piece is regulated and controlled.
2. The 4D printing method of the NiTiZr ternary alloy powder according to claim 1, wherein the NiTiZr ternary alloy powder is Ti with the grain size of 15-53 μm42.5Ni49.5Zr8The powder preferably has an average particle size of 33 μm.
3. The 4D printing method of the NiTi-based ternary shape memory alloy as claimed in claim 1, wherein the laser scanning strategy adopted by the selective laser melting technology is stripe partition and interlayer rotation, wherein the partition width is 4-10 mm, and the interlayer rotation angle is 16-67 °.
4. The method of 4D printing of a nitinol-based ternary shape memory alloy of claim 3, wherein the segment width is 10mm and the inter-layer rotation angle is 16 °.
5. The method for 4D printing of a nitinol-based ternary shape memory alloy of claim 1 wherein the selective laser melting technique uses printing parameters set to: the laser power is 160-280W, the scanning speed is 700-1300 mm/s, the scanning interval is 0.12mm, the powder spreading layer thickness is 0.03mm, and the substrate preheating temperature is 200 ℃.
6. The 4D printing method of the nitinol-based ternary shape memory alloy of claim 1, wherein the selective laser melting technique uses process parameters set to: the laser power is 250W, the scanning speed is 1000mm/s, and the laser energy density is 69.44J/mm3。
7. The method of 4D printing of a nitinol-based ternary shape memory alloy of claim 1 wherein the selective laser melting technique uses process parameters such that the laser fluence is greater than 34.19J/mm3。
8. The 4D printing method of the NiTi-based ternary shape memory alloy of claim 1, wherein in the printing process adopting the selective laser melting technology, the oxygen content of the equipment is less than or equal to 500ppm, argon is introduced as a protective gas, and the gas pressure is kept at 10-20 mbar.
9. The method of 4D printing of a nitinol-based ternary shape memory alloy of claim 1 wherein the maximum density for the printed component is 6.537g/cm3The maximum hardness is 5.3Gpa, and the martensite phase transformation peak temperature range is 91-104 ℃.
10. The method of 4D printing of a nitinol-based ternary shape memory alloy of claim 1 wherein the printed component has a phase composition comprising a (Ti, Zr) Ni phase, a ternary mesophase λ 1, and a monoclinic martensite phase B19'.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010562592.1A CN111842888A (en) | 2020-06-18 | 2020-06-18 | 4D printing method of nickel titanium based ternary shape memory alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010562592.1A CN111842888A (en) | 2020-06-18 | 2020-06-18 | 4D printing method of nickel titanium based ternary shape memory alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN111842888A true CN111842888A (en) | 2020-10-30 |
Family
ID=72987707
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202010562592.1A Pending CN111842888A (en) | 2020-06-18 | 2020-06-18 | 4D printing method of nickel titanium based ternary shape memory alloy |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN111842888A (en) |
Cited By (17)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112475318A (en) * | 2020-11-26 | 2021-03-12 | 华中科技大学 | 4D printing method for nickel-titanium alloy and titanium alloy multi-material |
| CN112807493A (en) * | 2020-12-31 | 2021-05-18 | 山东第一医科大学附属省立医院(山东省立医院) | Biliary tract implant and manufacturing method thereof |
| CN112974847A (en) * | 2021-02-08 | 2021-06-18 | 华南理工大学 | Core-shell structure titanium-nickel medical implant based on elastic modulus regulation and control, 4D printing forming method and application |
| CN113134630A (en) * | 2021-04-27 | 2021-07-20 | 山东大学 | Nickel-titanium shape memory alloy component and preparation method thereof |
| CN113199036A (en) * | 2021-04-20 | 2021-08-03 | 华南理工大学 | Ultrahigh superelasticity titanium-nickel shape memory alloy with functional element structure and 4D printing preparation method and application thereof |
| CN113351880A (en) * | 2021-05-31 | 2021-09-07 | 中国石油大学(北京) | Manufacturing method of nickel-titanium alloy component and nickel-titanium alloy component |
| CN113909493A (en) * | 2021-09-09 | 2022-01-11 | 中国地质大学（武汉） | Nickel-titanium alloy and neodymium-iron-boron alloy multi-material and 4D printing method and application thereof |
| CN113935241A (en) * | 2021-10-18 | 2022-01-14 | 吉林大学 | Laser selection melting NiTi phase transition temperature prediction algorithm based on Levenberg-Mar improved algorithm |
| CN113944564A (en) * | 2021-09-17 | 2022-01-18 | 中国地质大学（武汉） | Variable-aperture device based on 4D printing technology and preparation method thereof |
| CN114346259A (en) * | 2021-12-30 | 2022-04-15 | 华南理工大学 | Nickel-titanium shape memory alloy with stable memory function and suitable for human body bearing implant, and 4D printing method and application thereof |
| CN114535600A (en) * | 2022-01-11 | 2022-05-27 | 天津大学 | Method for optimizing CuAlNi memory alloy 4D printing process |
| CN114686724A (en) * | 2022-03-11 | 2022-07-01 | 华南理工大学 | Composite material with shape memory function and SLM (Selective laser melting) preparation method thereof |
| CN114769619A (en) * | 2022-03-08 | 2022-07-22 | 南京理工大学 | Laser additive manufacturing method for high-toughness titanium-based composite material with multiple reaction systems |
| CN114951692A (en) * | 2022-03-31 | 2022-08-30 | 华中科技大学 | Nickel-titanium energy-absorbing and vibration-damping three-cycle extremely-small curved surface lattice structure and preparation method thereof |
| CN115041706A (en) * | 2022-05-31 | 2022-09-13 | 中南大学 | Heat treatment method for improving comprehensive performance of 3D printing nickel-titanium-copper alloy |
| CN115070052A (en) * | 2022-05-18 | 2022-09-20 | 华南理工大学 | Novel binary-structure nickel-titanium shape memory alloy and 4D printing preparation method and application thereof |
| CN115961176A (en) * | 2022-11-25 | 2023-04-14 | 广东技术师范大学 | NiTiCu shape memory alloy and 4D printing method and application thereof |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008274439A (en) * | 2008-05-21 | 2008-11-13 | Akita Prefecture | W-ti-c-based composite body and production method therefor |
| JP2012214826A (en) * | 2011-03-31 | 2012-11-08 | Technology Research Institute Of Osaka Prefecture | Method for producing metallic glass molded body |
| CN108403256A (en) * | 2018-03-14 | 2018-08-17 | 华南理工大学 | The trivector expansion angiocarpy bracket and manufacturing method with memory effect based on 4D printings |
| CN109022920A (en) * | 2018-08-30 | 2018-12-18 | 中南大学 | A kind of 4D printing Ti-Ni marmem of flawless and preparation method thereof |
| CN109518103A (en) * | 2018-12-28 | 2019-03-26 | 武汉大学 | A method of Nitinol refrigeration efficiency is improved than, service life and temperature stability |
| CN109648082A (en) * | 2019-01-24 | 2019-04-19 | 华南理工大学 | A kind of 4D Method of printing of Ti-Ni marmem and application |
| CN110090954A (en) * | 2019-04-24 | 2019-08-06 | 中国石油大学(北京) | A kind of increasing material manufacturing NiTi marmem and preparation method thereof |
-
2020
- 2020-06-18 CN CN202010562592.1A patent/CN111842888A/en active Pending
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008274439A (en) * | 2008-05-21 | 2008-11-13 | Akita Prefecture | W-ti-c-based composite body and production method therefor |
| JP2012214826A (en) * | 2011-03-31 | 2012-11-08 | Technology Research Institute Of Osaka Prefecture | Method for producing metallic glass molded body |
| CN108403256A (en) * | 2018-03-14 | 2018-08-17 | 华南理工大学 | The trivector expansion angiocarpy bracket and manufacturing method with memory effect based on 4D printings |
| CN109022920A (en) * | 2018-08-30 | 2018-12-18 | 中南大学 | A kind of 4D printing Ti-Ni marmem of flawless and preparation method thereof |
| CN109518103A (en) * | 2018-12-28 | 2019-03-26 | 武汉大学 | A method of Nitinol refrigeration efficiency is improved than, service life and temperature stability |
| CN109648082A (en) * | 2019-01-24 | 2019-04-19 | 华南理工大学 | A kind of 4D Method of printing of Ti-Ni marmem and application |
| CN110090954A (en) * | 2019-04-24 | 2019-08-06 | 中国石油大学(北京) | A kind of increasing material manufacturing NiTi marmem and preparation method thereof |
Non-Patent Citations (1)
| Title |
|---|
| 冯昭伟等: "镍钛锆高温形状记忆合金的研究进展", 《材料导报》 * |
Cited By (26)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112475318A (en) * | 2020-11-26 | 2021-03-12 | 华中科技大学 | 4D printing method for nickel-titanium alloy and titanium alloy multi-material |
| CN112807493B (en) * | 2020-12-31 | 2022-04-22 | 山东第一医科大学附属省立医院(山东省立医院) | Biliary tract implant and manufacturing method thereof |
| CN112807493A (en) * | 2020-12-31 | 2021-05-18 | 山东第一医科大学附属省立医院(山东省立医院) | Biliary tract implant and manufacturing method thereof |
| CN112974847A (en) * | 2021-02-08 | 2021-06-18 | 华南理工大学 | Core-shell structure titanium-nickel medical implant based on elastic modulus regulation and control, 4D printing forming method and application |
| CN112974847B (en) * | 2021-02-08 | 2022-05-24 | 华南理工大学 | Core-shell structure titanium-nickel medical implant based on elastic modulus regulation and control, 4D printing forming method and application |
| CN113199036A (en) * | 2021-04-20 | 2021-08-03 | 华南理工大学 | Ultrahigh superelasticity titanium-nickel shape memory alloy with functional element structure and 4D printing preparation method and application thereof |
| CN113199036B (en) * | 2021-04-20 | 2022-06-10 | 华南理工大学 | Ultrahigh superelasticity titanium-nickel shape memory alloy with functional element structure and 4D printing preparation method and application thereof |
| CN113134630A (en) * | 2021-04-27 | 2021-07-20 | 山东大学 | Nickel-titanium shape memory alloy component and preparation method thereof |
| CN113351880A (en) * | 2021-05-31 | 2021-09-07 | 中国石油大学(北京) | Manufacturing method of nickel-titanium alloy component and nickel-titanium alloy component |
| CN113909493A (en) * | 2021-09-09 | 2022-01-11 | 中国地质大学（武汉） | Nickel-titanium alloy and neodymium-iron-boron alloy multi-material and 4D printing method and application thereof |
| CN113909493B (en) * | 2021-09-09 | 2023-02-17 | 中国地质大学（武汉） | Nickel-titanium alloy and neodymium-iron-boron alloy multi-material and 4D printing method and application thereof |
| CN113944564A (en) * | 2021-09-17 | 2022-01-18 | 中国地质大学（武汉） | Variable-aperture device based on 4D printing technology and preparation method thereof |
| CN113944564B (en) * | 2021-09-17 | 2022-09-20 | 中国地质大学（武汉） | Variable-aperture device based on 4D printing technology and preparation method thereof |
| CN113935241A (en) * | 2021-10-18 | 2022-01-14 | 吉林大学 | Laser selection melting NiTi phase transition temperature prediction algorithm based on Levenberg-Mar improved algorithm |
| CN113935241B (en) * | 2021-10-18 | 2024-04-30 | 吉林大学 | Laser selection melting NiTi phase transition temperature prediction method based on Levenberg-Mar improved algorithm |
| CN114346259A (en) * | 2021-12-30 | 2022-04-15 | 华南理工大学 | Nickel-titanium shape memory alloy with stable memory function and suitable for human body bearing implant, and 4D printing method and application thereof |
| CN114535600A (en) * | 2022-01-11 | 2022-05-27 | 天津大学 | Method for optimizing CuAlNi memory alloy 4D printing process |
| CN114535600B (en) * | 2022-01-11 | 2024-04-19 | 天津大学 | CuAlNi memory alloy 4D printing process optimization method |
| CN114769619A (en) * | 2022-03-08 | 2022-07-22 | 南京理工大学 | Laser additive manufacturing method for high-toughness titanium-based composite material with multiple reaction systems |
| CN114769619B (en) * | 2022-03-08 | 2024-04-05 | 南京理工大学 | High-strength and high-toughness titanium-based composite material multi-reaction system laser additive manufacturing method |
| CN114686724A (en) * | 2022-03-11 | 2022-07-01 | 华南理工大学 | Composite material with shape memory function and SLM (Selective laser melting) preparation method thereof |
| CN114951692A (en) * | 2022-03-31 | 2022-08-30 | 华中科技大学 | Nickel-titanium energy-absorbing and vibration-damping three-cycle extremely-small curved surface lattice structure and preparation method thereof |
| CN115070052A (en) * | 2022-05-18 | 2022-09-20 | 华南理工大学 | Novel binary-structure nickel-titanium shape memory alloy and 4D printing preparation method and application thereof |
| CN115041706A (en) * | 2022-05-31 | 2022-09-13 | 中南大学 | Heat treatment method for improving comprehensive performance of 3D printing nickel-titanium-copper alloy |
| CN115961176A (en) * | 2022-11-25 | 2023-04-14 | 广东技术师范大学 | NiTiCu shape memory alloy and 4D printing method and application thereof |
| CN115961176B (en) * | 2022-11-25 | 2024-04-30 | 广东技术师范大学 | NiTiCu shape memory alloy and 4D printing method and application thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN111842888A (en) | 4D printing method of nickel titanium based ternary shape memory alloy | |
| Alshataif et al. | Manufacturing methods, microstructural and mechanical properties evolutions of high-entropy alloys: a review | |
| Guo et al. | Selective laser melting additive manufacturing of pure tungsten: Role of volumetric energy density on densification, microstructure and mechanical properties | |
| CN108213422B (en) | Preparation method of carbon-containing high-entropy alloy composite material | |
| CN110090954B (en) | Additive manufacturing NiTi shape memory alloy and preparation method thereof | |
| Rong et al. | Formation of novel graded interface and its function on mechanical properties of WC1− x reinforced Inconel 718 composites processed by selective laser melting | |
| CN112935252B (en) | Method for preparing high-toughness eutectic high-entropy alloy based on selective laser melting technology | |
| Jia et al. | Selective laser melting additive manufacturing of TiC/Inconel 718 bulk-form nanocomposites: Densification, microstructure, and performance | |
| Chen et al. | In situ TiC/Inconel 625 nanocomposites fabricated by selective laser melting: Densification behavior, microstructure evolution, and wear properties | |
| CN113210629A (en) | AlCoCrFeNi2.1Eutectic high-entropy alloy and laser selective material increase manufacturing method thereof | |
| Ma et al. | Microstructure evolution and high-temperature oxidation behaviour of selective laser melted TiC/TiAl composites | |
| CN110303156A (en) | A kind of increasing material manufacturing and heat-treated sturcture regulation method of Titanium Alloys for Aviation complex component | |
| CN110983106B (en) | Method for inhibiting formation of needle-like martensite phase in 3D printing forming TC4 alloy structure | |
| Cao et al. | Laser metal deposition additive manufacturing of TiC/Inconel 625 nanocomposites: Relation of densification, microstructures and performance | |
| CN109022920A (en) | A kind of 4D printing Ti-Ni marmem of flawless and preparation method thereof | |
| Li et al. | Microstructure and mechanical properties of the Ni-B-Ti composite coating on TA2 prepared by pre-plating and laser remelting | |
| CN105728725B (en) | The method that 3D printing prepares multielement transition interface collaboration enhancing nickel-base composite material | |
| CN111451502B (en) | Partition regulation and control method for in-situ synthesized TiC-reinforced titanium-based composite material in additive manufacturing | |
| CN115418544A (en) | Precipitation type reinforced high-entropy high-temperature alloy and preparation method thereof | |
| CN110241419B (en) | Titanium alloy material with high-temperature oxidation resistant and wear-resistant coating on surface and application | |
| Zhao et al. | Metallurgical defect behavior, microstructure evolution, and underlying thermal mechanisms of metallic parts fabricated by selective laser melting additive manufacturing | |
| CN112935275B (en) | Electron beam fuse additive manufacturing method of gradient TiNi shape memory alloy | |
| KR20160071619A (en) | Method for manufacturing fe-based superalloy | |
| Liu et al. | Functionally Gradient Ti6Al4V-TiB Composite Produced by Spark Plasma Sintering | |
| Yang et al. | Microstructure Twinning and Mechanical Properties of Laser Melted Cu-10Sn Alloy for High Strength and Plasticity |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| WD01 | Invention patent application deemed withdrawn after publication |
Application publication date: 20201030 |
|
| WD01 | Invention patent application deemed withdrawn after publication |