CN115921889A - Nickel-titanium alloy with gradient function and preparation method and application thereof - Google Patents
Nickel-titanium alloy with gradient function and preparation method and application thereof Download PDFInfo
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- 229910001000 nickel titanium Inorganic materials 0.000 title claims abstract description 55
- 238000002360 preparation method Methods 0.000 title claims abstract description 10
- 238000000034 method Methods 0.000 claims abstract description 44
- 239000000956 alloy Substances 0.000 claims abstract description 25
- 230000008569 process Effects 0.000 claims abstract description 24
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 20
- 238000004519 manufacturing process Methods 0.000 claims abstract description 17
- 230000008859 change Effects 0.000 claims abstract description 12
- 239000000843 powder Substances 0.000 claims description 20
- 238000002844 melting Methods 0.000 claims description 16
- 230000008018 melting Effects 0.000 claims description 16
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 14
- 239000000758 substrate Substances 0.000 claims description 9
- 238000003892 spreading Methods 0.000 claims description 8
- 230000007480 spreading Effects 0.000 claims description 8
- 229910052786 argon Inorganic materials 0.000 claims description 7
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 4
- 239000001301 oxygen Substances 0.000 claims description 4
- 229910052760 oxygen Inorganic materials 0.000 claims description 4
- 238000005482 strain hardening Methods 0.000 claims description 4
- 238000000465 moulding Methods 0.000 claims description 3
- 239000007789 gas Substances 0.000 claims description 2
- 238000009689 gas atomisation Methods 0.000 claims description 2
- 230000001788 irregular Effects 0.000 claims description 2
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- 238000001291 vacuum drying Methods 0.000 claims description 2
- 230000006870 function Effects 0.000 abstract description 10
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- 238000001938 differential scanning calorimetry curve Methods 0.000 description 3
- 229910000734 martensite Inorganic materials 0.000 description 3
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- 238000005240 physical vapour deposition Methods 0.000 description 2
- 238000004663 powder metallurgy Methods 0.000 description 2
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- 229910001285 shape-memory alloy Inorganic materials 0.000 description 2
- 238000000137 annealing Methods 0.000 description 1
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- 238000005224 laser annealing Methods 0.000 description 1
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- 229910052751 metal Inorganic materials 0.000 description 1
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- HLXZNVUGXRDIFK-UHFFFAOYSA-N nickel titanium Chemical compound [Ti].[Ti].[Ti].[Ti].[Ti].[Ti].[Ti].[Ti].[Ti].[Ti].[Ti].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni] HLXZNVUGXRDIFK-UHFFFAOYSA-N 0.000 description 1
- 239000012299 nitrogen atmosphere Substances 0.000 description 1
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- 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
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Abstract
The invention discloses a nickel-titanium alloy with gradient functions and a preparation method and application thereof. The method comprises the following steps: a) Designing a plurality of groups of models by using three-dimensional modeling software, then taking one group of models as a base model according to requirements, and correspondingly stacking the rest models; b) According to the designed combined model, firstly, assigning process parameters to the base model according to requirements, and then sequentially assigning the process parameters to the stacked model; c) And preparing the gradient functional NiTi alloy workpiece by using laser. The invention can control the sequence and flow of laser scanning and manufacture the functionally graded NiTi alloy parts. The method ensures that the preparation of the NiTi part with the gradient is simple and easy to control, and the prepared NiTi alloy has good gradual phase change characteristics.
Description
Technical Field
The invention belongs to the field of nickel-titanium alloy, and relates to a nickel-titanium alloy with a gradient function, and a preparation method and application thereof.
Background
NiTi alloys are the most widely used shape memory alloys due to their excellent shape memory effect and superelasticity. It has been demonstrated that its maximum recoverable strain is as high as 8%. Meanwhile, the NiTi alloy has low Young modulus, high damping and good biocompatibility and corrosion resistance, so that the NiTi alloy becomes an excellent candidate material in the fields of aerospace and bioengineering and the field of automobile industry, and is often used for skillful design of some key structures. These unique properties are the reversible thermoelastic martensitic transformation between the source B2 phase and the B19' phase. However, the narrow Martensitic Transformation Temperature (MTT) presents a certain difficulty in controlling, driving shape memory, since too short a transformation means that the shape recovery process is too fast. Second, the lack of strain hardening on the strain-stress curve also hinders the use of NiTi alloys. Therefore, in recent years, a functionally graded NiTi alloy characterized by the occurrence of a gradual martensitic transformation upon heating or cooling has been considered as an effective method for solving the above-mentioned problems.
Currently, to achieve a gradual phase transformation, it is common to introduce a specific microstructure, composition, or geometric gradient in the NiTi alloy to achieve a functionally graded property. Related techniques and methods include Physical Vapor Deposition (PVD), diffusion annealing, chemical processing, laser annealing, and the like. However, in general, these methods are complicated to implement and it is difficult to control the phase transition temperature and the precise change of the gradient well.
In recent years, an additive manufacturing method (also called 3D printing technology) is highly regarded in the field of functional structural member manufacturing, and compared with a traditional processing method (such as casting, forging and rolling or powder metallurgy), the 3D printing is based on a manufacturing idea of layered manufacturing and layer-by-layer superposition, and a three-dimensional physical entity with any complex shape can be rapidly manufactured by direct driving of a digital model. The selective laser melting technology is one of additive manufacturing, CAD/CAE software is used for modeling, a complex model is sliced in the software, each slice comprises all geometric information of the slice layer, a file is stored in an STL format, and then the slice is guided into printing equipment, and metal powder is melted layer by high-energy laser beams until a complete part is finally formed.
The NiTi alloy is an excellent material with shape memory function, and can be used for manufacturing structural parts with special functions, but the precise structure and components of the NiTi alloy are difficult to control by the traditional manufacturing methods, such as forging, casting and traditional powder metallurgy; the selective laser melting method has the advantage of accurately manufacturing a complex-shaped structure, but the manufactured part of the NiTi alloy prepared at present has single function and narrow phase transition temperature, and the NiTi structural part with the gradient function is difficult to manufacture.
Disclosure of Invention
In order to solve the technical problems in the prior art, the invention provides a preparation method of a nickel-titanium alloy with gradient functions, which comprises the following steps: and constructing a combined model, taking one group of models as a base model, stacking the rest models in the base model, and performing laser scanning and molding according to the stacking sequence of the models in the combined model by adopting a selective laser melting method to prepare the gradient functional nickel-titanium alloy.
Preferably, the laser power of at least one of the residual models is different from that of the substrate model, and the laser power of each model in the residual models changes in a gradient manner; for example, the gradient change may be a regular or irregular gradient change; such as an isocratic gradient.
According to an embodiment of the invention, the model is constructed by CAD/CAE modeling software.
According to an embodiment of the invention, each model of the combined model may be independently selected from the following process parameters: the laser power is 10-95W, the spot diameter is 30-50 μm, the scanning speed is 250-800 mm/s, the scanning interval is 80-110 μm, and the powder layer thickness is 25-30 μm.
According to an embodiment of the present invention, the scanning strategy of the laser scanning may be a checkerboard scanning or an island scanning.
For example, each of the combined models may be independently selected from the following process parameters: the scanning laser power (P) is 40-70W, the spot diameter (d) is 35-45 μm, the scanning speed (v) is 250-500 mm/s, the scanning interval (h) is 90-100 μm, and the powder spreading layer thickness (t) is 25-30 μm.
Illustratively, the number of models of the combined model may be 3, 4, 5, 6, 7, 8, 9, 10.
According to an exemplary embodiment of the present invention, the number of models of the combined model is 7 groups, model 1 is used as a base model, the rest of models are stacked in the working section,
the process parameters of model 1 were: the laser power is 60W, the scanning speed is 440mm/s, the scanning distance is 110 mu m, the powder spreading layer is 25 mu m thick, and the scanning strategy is checkerboard scanning;
the laser power of the models 2, 3, 4, 5, 6 and 7 is 15W, 30W, 45W, 60W, 75W and 90W respectively, and the rest parameters are the same as or different from those of the model 1.
According to an exemplary embodiment of the present invention, the number of models of the combined model is 7 groups, model 1 is used as a stack model, the rest models are used as base models, the tension member working sections of model 1 are stacked in the base models,
the process parameters of model 1 were: the laser power is 60W, the scanning speed is 440mm/s, the scanning distance is 110 mu m, the powder spreading layer is 25 mu m thick, and the scanning strategy is checkerboard scanning;
the laser power of the models 2, 3, 4, 5, 6 and 7 is 15W, 30W, 45W, 60W, 75W and 90W respectively, and the rest parameters are the same as or different from those of the model 1.
According to an embodiment of the invention, the powder for powder laying is a pre-alloyed near-equal atomic ratio NiTi powder prepared by an atomic gas atomization method, the particle diameter of the powder is distributed in the range of 15-53 mu m, and the powder is subjected to vacuum drying treatment before use, preferably 60-120 ℃ for 4-5 hours.
According to the embodiment of the invention, the preparation method further comprises the step of forming the nickel-titanium alloy on the substrate after laser scanning to obtain the gradient functional nickel-titanium alloy.
According to the embodiment of the invention, the oxygen content is ensured to be less than or equal to 500ppm (namely, the value of the oxygen content displayed by an oxygen sensor in the selective laser melting equipment is less than or equal to 0.05%) in the forming process; preferably, argon is used as a shield, and the gas pressure is kept between 10 and 20mbar.
According to an embodiment of the invention, the substrate is a NiTi alloy substrate.
According to an embodiment of the invention, during the scanning and forming process, the laser will preferentially scan the layer on which the base model is located, and then sequentially scan the layers on which the overlay model is located in the order of the stack model.
According to an embodiment of the present invention, the selective laser melting is performed in a known selective laser melting molding apparatus.
According to an exemplary embodiment of the invention, the preparation method of the gradient functional nickel-titanium alloy comprises the following steps:
a) Designing a plurality of groups of models by using CAD/CAE modeling software, then taking one group of models as a base model according to requirements, and correspondingly stacking the rest models;
b) Placing three-dimensional STL data of a product in selective laser melting equipment according to the combined model designed in the step a), firstly carrying out assignment of process parameters on a substrate model according to requirements, and then sequentially carrying out assignment of process parameters on a stacked model;
c) And printing the combined model on a substrate by using laser to prepare the nickel-titanium alloy with the gradient function.
The invention also provides a gradient functional nickel-titanium alloy which has a gradual phase change characteristic.
For example, the gradient function nitinol has multiple strain platforms.
For example, the gradient functional nickel titanium alloy has significant strain hardening characteristics when cyclically stretched.
Preferably, the gradient functional nickel-titanium alloy is prepared by the method.
The invention also provides application of the nickel-titanium alloy with the gradient function in the fields of aerospace, bioengineering or automobile industry.
The invention has the advantages of
Aiming at the technical problem that a gradient NiTi alloy workpiece is difficult to manufacture by selective laser melting, the invention provides an iterative scanning method for preparing a NiTi alloy based on a selective laser melting method. The invention uses selective laser melting technology, draws models with different shapes by matching with CAD/CAE software, iterates and slices the models with different shapes, and uses laser energy to change the microcosmic components and the structural characteristics of the NiTi alloy to perform selective scanning, wherein the scanning times are the number of iterated models, so as to generate phase change and mechanical functional characteristics different from those of the existing homogeneous NiTi shape memory alloy, and obtain a nickel-titanium alloy product with gradient change. The alloy part has effectively improved strength and comprehensive mechanical performance, continuous superelasticity and shape memory performance, and wide and complicated application range.
Drawings
FIG. 1 is a schematic diagram of an iterative scanning strategy adopted for preparing a gradient NiTi alloy material;
FIG. 2 is a schematic representation of an iterative model employed to prepare tensile samples of the gradient NiTi alloy material;
FIG. 3 is a DSC curve of the gradient NiTi alloy material prepared in example 1;
FIG. 4 is a tensile mechanical curve of a gradient NiTi alloy material prepared in example 1;
FIG. 5 is a cyclic stretch-unload mechanics curve for the preparation of a gradient NiTi alloy material of example 1.
Detailed Description
The technical solution of the present invention will be further described in detail with reference to specific embodiments. It is to be understood that the following examples are only illustrative and explanatory of the present invention and should not be construed as limiting the scope of the present invention. All the technologies realized based on the above-mentioned contents of the present invention are covered in the protection scope of the present invention.
Unless otherwise indicated, the raw materials and reagents used in the following examples are all commercially available products or can be prepared by known methods.
As shown in fig. 1, a schematic diagram of model stacking is shown, wherein model a is a base model and model B is a stacked model. A gradient tensile member is manufactured according to the strategy, as shown in fig. 2, a tensile member model 1 is designed in three-dimensional design software, and then models 2, 3.
Conditions for phase transition temperature test in examples and comparative examples: the transition temperature was measured in a nitrogen atmosphere using a differential scanning calorimeter model Netzsch DSC 200F3, a heating/cooling rate of 10 ℃/min, a test temperature range of-50 to 180 ℃.
Test conditions of the tensile test: tensile tests were carried out according to the national standard GB/T228.1-2010 using a universal tester model INSTRON3369 at a constant loading speed of 1mm/min and at room temperature (25 ℃) (using an extensometer throughout the process).
Test conditions for cyclic loading-unloading experiments: on a universal tester model INSTRON3369 at a strain increment of 0.3% and 10 -3 s -1 Strain rate of (2) to perform cyclic stretchingAnd (4) testing.
Example 1
As shown in fig. 1, a schematic diagram of model stacking is shown, wherein model a is a base model and model B is a stacked model. Manufacturing a gradient tensile member according to the strategy, as shown in fig. 2, designing a tensile member model 1 in three-dimensional design software, taking the tensile member model as a base model, and then designing models 2, 3, 4, 5, 6 and 7 to be sequentially stacked in a tensile member working section; then the combined model is introduced into selective laser melting equipment, and the process parameters of the model 1 are as follows: the laser power is 60W, the scanning speed is 440mm/s, the scanning interval is 110 mu m, the powder spreading layer is 25 mu m thick, the scanning strategy is checkerboard scanning, and the diameter of a laser spot is 30 mu m. The laser parameters of the models 2, 3, 4, 5, 6 and 7 are respectively 15W, 30W, 45W, 60W, 75W and 90W, and other process parameters are kept the same as those of the model 1; and under the protection of argon, forming by laser scanning.
In order to verify whether the tensile member is a gradient member, the phase transition temperature is measured by using DSC, and the result is shown in fig. 3; the stress-strain curve is tested by using a universal tester, and a tensile test and a cyclic loading-unloading test are respectively carried out, and the results are shown in figures 4 and 5:
from the DSC curve of (a) in FIG. 3, it can be seen that the samples of the overlay models 2, 3, 4, 5, 6, 7, under the application of laser powers varying from 15W, 30W, 45W, 60W, 75W and 90W, have phase transition temperatures, especially M s A clear gradual increase trend occurs, while the DSC curve of the complete sample of fig. 3 (b) shows a very wide phase transition region, roughly the superposition of the phase transition temperatures of the superposition models 2, 3, 4, 5, 6, 7. The manufactured tensile member is proved to have a gradual phase change characteristic; it is apparent from the tensile curve of fig. 4 that there are multiple strain plateaus, unlike the stress-strain curve of conventional NiTi alloys; as can be seen from the cyclic tensile curve of fig. 5, there is a distinct strain hardening characteristic.
Example 2
As shown in fig. 1, a schematic diagram of model stacking is shown, wherein model B is a base model and model a is a stacking model. Manufacturing a gradient tensile member according to the strategy, as shown in fig. 2, designing a tensile member model 1 in three-dimensional design software, taking the model as a stacked model, then designing models 2, 3, 4, 5, 6 and 7, sequencing the models into a base model in sequence, and stacking the tensile member working sections of the model 1 on the base models 2, 3, 4, 5, 6 and 7; then the combined model is introduced into selective laser melting equipment, and the process parameters of the model 1 are as follows: the laser power is 60W, the scanning speed is 440mm/s, the scanning interval is 110 mu m, the powder spreading layer is 25 mu m thick, the scanning strategy is checkerboard scanning, and the diameter of a laser spot is 30 mu m. The laser parameters of the models 2, 3, 4, 5, 6 and 7 are respectively 15W, 30W, 45W, 60W, 75W and 90W, and other process parameters are kept the same as those of the model 1; under the protection of argon, the gradient workpiece is formed by laser scanning and tested.
Example 3
As shown in fig. 1, a schematic diagram of model stacking is shown, wherein model a is a base model and model B is a stacked model. Manufacturing a gradient tensile member according to the strategy, as shown in fig. 2, designing a tensile member model 1 in three-dimensional design software, taking the tensile member model as a base model, then designing models 2, 3, 4, 5, 6 and 7, and sequentially stacking the models in a tensile member working section; then the combined model is introduced into selective laser melting equipment, and the process parameters of the model 1 are as follows: the laser power is 60W, the scanning speed is 440mm/s, the scanning interval is 110 mu m, the powder layer thickness is 25 mu m, the scanning strategy is checkerboard scanning, and the laser spot diameter is 30 mu m. The laser parameters of the models 2, 3, 4, 5, 6 and 7 are respectively 15W, 30W, 45W, 60W, 75W and 90W, the scanning intervals are all 80 μm, and other process parameters are kept the same as those of the model 1; under the protection of argon, the gradient workpiece is formed by laser scanning and tested.
Example 4
As shown in fig. 1, a schematic diagram of model stacking is shown, wherein model a is a base model and model B is a stacked model. Manufacturing a gradient tensile member according to the strategy, as shown in fig. 2, designing a tensile member model 1 in three-dimensional design software, taking the tensile member model as a base model, then designing models 2, 3, 4, 5, 6 and 7, and sequentially stacking the models in a tensile member working section; then the combined model is introduced into selective laser melting equipment, and the process parameters of the model 1 are as follows: the laser power is 60W, the scanning speed is 440mm/s, the scanning interval is 110 mu m, the powder spreading layer is 25 mu m thick, the scanning strategy is checkerboard scanning, and the diameter of a laser spot is 30 mu m. The laser parameters of the models 2, 3, 4, 5, 6 and 7 are respectively 15W, 30W, 45W, 60W, 75W and 90W, the laser scanning strategy is changed into island scanning, and other process parameters are kept the same as the model 1; under the protection of argon, the gradient workpiece is formed by laser scanning and tested.
Example 5
As shown in fig. 1, a schematic diagram of model stacking is shown, wherein model a is a base model and model B is a stacked model. Manufacturing a gradient tensile member according to the strategy, as shown in fig. 2, designing a tensile member model 1 in three-dimensional design software, taking the tensile member model as a base model, then designing models 2, 3, 4, 5, 6 and 7, and sequentially stacking the models in a tensile member working section; then the combined model is introduced into selective laser melting equipment, and the process parameters of the model 1 are as follows: the laser power is 60W, the scanning speed is 440mm/s, the scanning interval is 110 mu m, the powder spreading layer is 25 mu m thick, the scanning strategy is checkerboard scanning, and the diameter of a laser spot is 30 mu m. The laser parameters of the models 2, 3, 4, 5, 6 and 7 are respectively 15W, 30W, 45W, 60W, 75W and 90W, the scanning speeds are respectively 100, 200, 300, 400, 500, 600 and 700mm/s, and other process parameters are kept the same as the model 1; under the protection of argon, the gradient type laser scanning forming is also a gradient type product through testing.
The embodiments of the present invention have been described above. However, the present invention is not limited to the above embodiment. Any modification, equivalent replacement, or improvement made without departing from the spirit and principle of the present invention shall fall within the protection scope of the present invention.
Claims (10)
1. A method for preparing a gradient functional nickel-titanium alloy is characterized by comprising the following steps: and constructing a combined model, taking one group of models as a base model, stacking the rest models in the base model, and performing laser scanning and molding according to the stacking sequence of the models in the combined model by adopting a selective laser melting method to prepare the gradient functional nickel-titanium alloy.
2. The method according to claim 1, wherein at least one of the remaining patterns has a laser power different from that of the base pattern, and the laser power of each of the remaining patterns varies in a gradient manner; for example, the gradient change may be a regular or irregular gradient change; such as an arithmetic gradient.
3. The method of manufacturing of claim 1 or 2, wherein the model is constructed by CAD/CAE modeling software.
4. The method of any one of claims 1-3, wherein each model in the combined model is independently selected from the following process parameters: the laser power is 10-95W, the spot diameter is 30-50 μm, the scanning speed is 250-800 mm/s, the scanning interval is 80-110 μm, and the powder layer thickness is 25-30 μm.
5. Preparation method according to any one of claims 1 to 4, characterized in that the scanning strategy of the laser scanning is a checkerboard scanning or an island scanning.
6. The method for preparing according to any one of claims 1 to 5, wherein the powder for spreading is a pre-alloyed near-equal atomic ratio NiTi powder prepared by atomic gas atomization, the particle diameter of the powder is distributed in the range of 15 to 53 μm, and the powder is subjected to vacuum drying treatment before use.
7. The method according to any one of claims 1-6, further comprising laser scanning and then forming the alloy on a substrate to obtain the gradient functional nickel-titanium alloy.
Preferably, the oxygen content is ensured to be less than or equal to 500ppm in the forming process; preferably, argon is used as a shield, and the gas pressure is kept between 10 and 20mbar.
Preferably, the substrate is a NiTi alloy substrate.
Preferably, during the scanning and forming process, the laser will preferentially scan the layer on which the base model is located, and then sequentially scan the layers on which the overlay model is located in the order of stacking the models.
8. A gradient functional nickel titanium alloy, which is characterized in that the gradient functional nickel titanium alloy has a gradual phase change characteristic.
9. The gradient functional nickel titanium alloy of claim 8, wherein the gradient functional nickel titanium alloy has a plurality of strain platforms.
For example, the gradient functional nickel titanium alloy has significant strain hardening characteristics when cyclically stretched.
Preferably, the gradient functional nickel titanium alloy is prepared by the method of any one of claims 1 to 7.
10. Use of the gradient functional nickel titanium alloy of claim 8 or 9 in the aerospace, bioengineering or automotive industry field.
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| CN113145859A (en) * | 2021-04-07 | 2021-07-23 | 山东大学 | Method for reducing process sensitivity of phase change of nickel-titanium alloy melted in selective laser area |
| CN113134630A (en) * | 2021-04-27 | 2021-07-20 | 山东大学 | Nickel-titanium shape memory alloy component and preparation method thereof |
| CN113210626A (en) * | 2021-05-13 | 2021-08-06 | 江苏海宇机械有限公司 | Method for 4D printing of functionally graded titanium-nickel shape memory alloy component |
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