Periodic gradient heterostructure titanium-based amorphous alloy and laser melting preparation method thereof
By constructing a periodic gradient heterostructure through multi-stage laser melting and solidification, the problem of synergistic optimization of room temperature brittleness and strength-plasticity in titanium-based amorphous alloys was solved, thus achieving a comprehensive improvement in the mechanical properties of titanium-based amorphous alloys.
Patent Information
- Authority / Receiving Office
- CN · China
- Patent Type
- Applications(China)
- Current Assignee / Owner
- Filing Date
- 2026-01-14
- Publication Date
- 2026-04-14
AI Technical Summary
Titanium-based amorphous alloys are prone to brittle fracture at room temperature, and existing heterostructure construction techniques cannot achieve synergistic optimization of strength and plasticity, which limits their large-scale application in high-end engineering fields.
Through multi-stage laser melting and solidification, using a single-stage sequential melting and solidification process, and by controlling the laser scanning strategy and process parameters, a periodic gradient heterostructure is constructed, including single orientation and composite orientation, forming an alternating arrangement of "soft area-hard area", thereby achieving a synergistic improvement in strength and plasticity.
It significantly improves the fracture strength and elongation of titanium-based amorphous alloys, achieving synergistic optimization of strength and plasticity, with a fracture strength of 1469 MPa and an elongation of 9.33%.
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Figure CN121852897A_ABST
Abstract
Description
Technical Field
[0001] This invention relates to the field of metallic materials technology, specifically to a periodic gradient heterostructure titanium-based amorphous alloy and its laser melting and solidification preparation method. Background Technology
[0002] Titanium-based amorphous alloys, with their low density, high specific strength, excellent corrosion resistance, and biocompatibility, have shown great application potential in biomedicine (such as implantable / interventional devices like bone screws and surgical scalpels), aerospace (such as miniature transmission gears and pressure sensors), and electronic devices. However, when titanium-based amorphous alloys yield under load at room temperature, strain easily concentrates within a narrow shear band. This shear band tends to expand rapidly in a single direction, accompanied by significant stress concentration, leading to shear band localization and stress softening. This directly results in titanium-based amorphous alloys exhibiting prominent room-temperature brittleness and processing softening problems. When used as structural materials, they are highly susceptible to catastrophic brittle fracture without warning, severely restricting their large-scale application in high-end engineering fields.
[0003] To address the aforementioned performance bottlenecks, existing technologies employ a heterostructure construction approach within titanium-based amorphous alloys to improve their mechanical properties. However, these heterostructure construction technologies suffer from several drawbacks: In laser melting processes, technological development focuses solely on the impact of single parameters such as laser power on material structure, making it difficult to achieve precise control over the alloy's mechanical properties. Furthermore, during multi-stage laser melting operations, localized crystallization is prone to occur, damaging the matrix properties of the amorphous alloy. Additionally, the non-uniformity of the thermal process causes disordered fluctuations in the crystal size and density gradient of the heat-affected zone, hindering the synergistic optimization of alloy strength, plasticity, and surface properties. On the other hand, surface mechanical polishing technology not only has a shallow depth of action, improving only surface properties and failing to meet the overall mechanical performance requirements of load-bearing structural components, but also, due to the high reactivity and low thermal conductivity of titanium-based amorphous alloys, can lead to surface burns and microcracks during processing.
[0004] Therefore, there is an urgent need to develop a technical solution that can synergistically improve the strength and plasticity of titanium-based amorphous alloys in order to improve the overall mechanical properties of titanium-based amorphous alloys. Summary of the Invention
[0005] The purpose of this invention is to solve the technical problems of room temperature brittleness and softening during processing of titanium-based amorphous alloys, and the inability of existing heterostructure construction techniques to achieve synergistic optimization of strength and plasticity. This invention provides a periodic gradient heterostructure titanium-based amorphous alloy and its laser melting and solidification preparation method. By controlling the scanning strategy of laser melting and solidification, the periodic gradient heterostructure of titanium-based amorphous alloys can be precisely controlled, thereby improving its comprehensive mechanical properties and achieving synergistic optimization of strength and plasticity.
[0006] The above-mentioned objective of the present invention is achieved through the following technical solution:
[0007] A laser melting and solidification method for preparing a periodically gradient heterostructure titanium-based amorphous alloy includes the following steps:
[0008] A multi-pass laser melting and solidification process is performed on a titanium-based amorphous alloy. Each laser pass is arranged parallel to the surface of the titanium-based amorphous alloy, employing a single-pass sequential melting and solidification method with consistent process parameters for each laser pass. During this multi-pass laser melting and solidification process, a periodic gradient heterostructure is designed for distribution and orientation. This distribution and orientation includes single orientation and composite orientation. The angle of the single orientation is 30° or 60°, and the angle combination of the composite orientation is a combination of 60° and 300°. The angle is the angle between the extension direction of the laser scanning trajectory and the length direction of the titanium-based amorphous alloy plate itself. After the multi-pass laser melting and solidification process, the periodic gradient heterostructure titanium-based amorphous alloy is obtained. The laser power of each single laser pass is 700-800 W, the scanning speed is 120-180 mm / s, and the center-to-center distance between adjacent laser passes is 0.8-1.2 mm.
[0009] In this invention, after a single laser beam is applied to a titanium-based amorphous alloy, a clear gradient heterostructure is formed along the depth direction, specifically exhibiting a hierarchical distribution of the molten pool amorphous region, a heat-affected zone with a crystalline-amorphous composite structure, and the matrix amorphous region. This structure is formed due to the core characteristic of laser melting and solidification: the cooling rate inside the molten pool can reach 10... 3 The extremely rapid cooling rate of K / s creates a significant temperature gradient in the molten pool and its heat-affected zone, resulting in distinct differences in the thermal history experienced by different depth regions of the material. This ultimately promotes the spontaneous formation of gradient heterostructures along the depth direction of the alloy. Simultaneously, when multiple lasers scan parallel to the surface of the titanium-based amorphous alloy at a center-to-center spacing of 0.8-1.2 mm, each laser can independently form a solidified hard region (the molten pool amorphous region and the heat-affected zone) in the horizontal direction. A certain width of soft matrix region is reserved between adjacent solidified hard regions, ultimately forming a regular alternating arrangement of "hard region-soft region-hard region-soft region" on the surface of the titanium-based amorphous alloy, thus achieving the fabrication of a periodic gradient heterostructure.
[0010] Given that the distribution and orientation of heterostructures in titanium-based amorphous alloys affect the mechanical properties of the alloys, this invention utilizes the flexible controllability of laser melting technology. On the one hand, by adjusting process parameters such as laser power and scanning speed, the temperature field distribution is precisely controlled, enabling controllable adjustment of the morphology and size of gradient heterostructures. On the other hand, the distribution mode and orientation state of gradient heterostructures are designed collaboratively. By controlling the spatial arrangement and scanning direction between laser passes, the gradient heterostructures are guided to form a preset specific configuration, thereby achieving a synergistic improvement in the tensile strength and plasticity of the alloy.
[0011] Furthermore, the titanium-based amorphous alloy is a titanium-based amorphous alloy plate, preferably Ti. 33 Zr 30 Cu9Ni 5.3 Be 22.6 Titanium-based amorphous alloy plate.
[0012] Furthermore, the thickness of the titanium-based amorphous alloy plate is greater than the maximum melt pool depth of single-pass and multi-pass laser melting.
[0013] Furthermore, the thickness of the titanium-based amorphous alloy plate is 1.5-2.5 mm, preferably 2 mm. This thickness range is greater than the maximum melt pool depth of single-pass and multi-pass laser melting, which can effectively prevent the plate from being burned through by the laser and ensure the integrity of the heterostructure. At the same time, it can completely cover the entire area of the amorphous region of the melt pool, the heat-affected zone, and the amorphous region of the matrix, which can fully meet the characterization requirements of the gradient characteristics in the depth direction of the material, and facilitate the subsequent accurate analysis of the performance and morphology of the gradient heterostructure.
[0014] Furthermore, the process of pretreating the titanium-based amorphous alloy before performing multiple laser melting and solidification processes also includes a pretreatment step.
[0015] Furthermore, the pretreatment includes the steps of polishing and cleaning.
[0016] Specifically, the pretreatment includes sequentially performing fine sandpaper polishing, acetone ultrasonic cleaning, and ethanol ultrasonic cleaning.
[0017] Furthermore, the preprocessing process also includes steps for analysis and testing.
[0018] Furthermore, the analysis and testing were conducted using X-ray diffraction analysis, which confirmed that the titanium-based amorphous alloy has an amorphous structure.
[0019] In this specific implementation, a titanium-based amorphous alloy plate is selected as the matrix material. It undergoes pretreatment, first by polishing with fine sandpaper to ensure uniform surface roughness, followed by ultrasonic cleaning with acetone and ethanol to remove surface oil, impurities, and other contaminants. This ensures a clean, contaminant-free surface, preventing surface impurities from affecting the quality and structural uniformity of the molten pool during subsequent laser melting and solidification. After cleaning, X-ray diffraction analysis confirms the plate's pure amorphous structure, ensuring the initial properties of the matrix material meet requirements.
[0020] Furthermore, the wavelength of the single-channel laser is 1065-1080 nm, and the spot diameter is 1.5-2.5 mm.
[0021] Furthermore, the multi-stage laser melting and solidification process is carried out in an argon atmosphere with an argon flow rate of 4-6 L / min. If the argon flow rate is too low, the protective atmosphere is insufficient, and the alloy is prone to oxidation, damaging the amorphous structure and mechanical properties. If the argon flow rate is too high, the strong gas flow will carry away a large amount of heat from the molten pool, changing the local temperature field distribution, reducing the actual cooling rate, affecting the formation of amorphous phases and the precipitation of crystalline phases, and also disturbing the molten pool, resulting in irregular surface morphology and interfering with subsequent microstructure analysis.
[0022] Preferably, the laser power of a single laser is 750 W, the scanning speed is 150 mm / s, and the center-to-center distance between adjacent lasers is 1 mm.
[0023] The 700-800 W laser power range balances the need for effective melting and solidification with the preservation of the amorphous matrix, precisely adapting to the construction of periodic heterostructures. It avoids the problem of heat-affected zones overlapping due to excessive overlap between adjacent passes, and leverages the rapid cooling process to ensure the amorphous structure of the molten pool in the melting region is maintained. Simultaneously, it creates a gradient hardness distribution from hard to soft regions, laying the structural foundation for subsequent optimization of material mechanical properties through orientation control. If the laser power is below 700 W, insufficient energy prevents the formation of an effective hard region, causing the heterostructure to lose its periodicity. At 750 W, the energy density is moderate, forming a molten pool with a depth of 0.2-0.3 mm and a width of 1-1.2 mm, achieving a high degree of matching with the spacing between adjacent passes. If the laser power exceeds 800 W, an excessively wide molten pool leads to pass overlap, heat accumulation causing crystalline phase precipitation, and damaging the amorphous matrix and periodic structure.
[0024] Controlling the laser scanning speed within the high-speed range of 120-180 mm / s can avoid thermal interference between multiple passes, establish a stable free volume gradient, and meet the efficiency requirements of periodic heterostructure fabrication. On the one hand, the high scanning speed can significantly shorten the heat input time of a single pass, promoting rapid dissipation of residual heat from the previous pass and preventing thermal superposition with subsequent passes. On the other hand, the high speed creates a significant cooling rate gradient, driving the molten pool to exhibit a distribution characteristic of increasing free volume concentration and decreasing hardness along the depth direction, thereby strengthening the periodic structural properties of alternating "soft-hard" regions. If the scanning speed is lower than 120 mm / s, it is easy to cause heat accumulation between passes, resulting in excessive overlap of the molten zones and inducing crystalline phase precipitation, destroying the amorphous matrix and periodic structure. If the scanning speed is higher than 180 mm / s, insufficient energy transfer will lead to an excessively shallow molten pool depth, causing the gradient structure to disappear and the periodic arrangement to break, neither of which can achieve the core objective of optimizing mechanical properties by controlling the orientation of heterostructures under multi-pass melting and solidification processes.
[0025] In one embodiment of the present invention, a 1 mm center-to-center spacing between adjacent lasers is selected in the multi-pass laser melting process, which can precisely achieve the goal of constructing a periodic soft-hard heterostructure. At a laser power of 750 W, the molten pool width is approximately 1-1.2 mm. The 1 mm center-to-center spacing allows for slight connection between the edges of adjacent molten pools without excessive overlap. This avoids the problem of overlapping heat-affected zones caused by excessively small spacing, which can induce crystalline phase precipitation. It also prevents uneven distribution of the "hard-soft" region due to excessively large spacing, which could lead to fracture of the periodic structure. If the spacing is too small, it will directly damage the integrity of the amorphous alloy matrix; if the spacing is too large, it will fail to effectively improve the mechanical properties. Neither of these approaches can meet the core requirement of optimizing the comprehensive material properties through orientation design in the multi-pass melting process.
[0026] This invention also protects a periodic gradient heterostructure titanium-based amorphous alloy prepared by the above-described laser melting and solidification method.
[0027] Compared with the prior art, the above-described technical solution of the present invention has the following advantages:
[0028] This invention provides a method for controlling the mechanical properties of titanium-based amorphous alloys by preparing periodic gradient heterostructures through laser melting and solidification using a controlled scanning strategy. The aim is to address the technical problems of catastrophic brittle fracture and the difficulty in synergistically optimizing strength and plasticity in titanium-based amorphous alloys at room temperature. Through precise design of a multi-channel laser scanning strategy, this invention constructs a periodically distributed gradient heterostructure of "soft-hard regions" on the surface of the titanium-based amorphous alloy matrix. After laser melting and solidification, the fracture strength of the titanium-based amorphous alloy reaches 1469 MPa, and the elongation increases to 9.33%, achieving a synergistic improvement in both strength and plasticity. Attached Figure Description
[0029] Figure 1 This is a schematic diagram of the periodic gradient heterostructure formed in the depth direction and horizontal direction of the titanium-based amorphous alloy plate of the present invention; wherein, (a) is the depth direction and (b) is the horizontal direction.
[0030] Figure 2 Ti, as a control example 33 Zr 30 Cu9Ni 5.3 Be 22.6 XRD patterns of titanium-based amorphous alloy plates, periodic gradient heterostructure titanium-based amorphous alloy plates prepared in Examples 1-3 and Comparative Examples 1-3.
[0031] Figure 3 A schematic diagram showing the design of the distribution orientation of the periodic gradient heterostructures in Examples 1-3 and Comparative Examples 1-3, with the stretching direction as shown.
[0032] Figure 4 Ti, as a control example33 Zr 30 Cu9Ni 5.3 Be 22.6 Stress-strain curves of titanium-based amorphous alloy plates, periodic gradient heterostructure titanium-based amorphous alloy plates prepared in Examples 1-3 and Comparative Examples 1-3. Detailed Implementation
[0033] 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 pertains. The terminology used herein in the description of the invention is for the purpose of describing particular embodiments only and is not intended to be limiting of the invention. The term "and / or" as used herein includes any and all combinations of one or more of the associated listed items.
[0034] This invention provides a laser melting and solidification method for preparing a periodically gradient heterostructure titanium-based amorphous alloy, comprising the following steps:
[0035] A multi-pass laser melting and solidification process is performed on a titanium-based amorphous alloy. Each laser pass is arranged parallel to the surface of the titanium-based amorphous alloy, employing a single-pass sequential melting and solidification method with consistent process parameters for each laser pass. During this multi-pass laser melting and solidification process, a periodic gradient heterostructure is designed for distribution and orientation. This distribution and orientation includes single orientation and composite orientation. The angle of the single orientation is 30° or 60°, and the angle combination of the composite orientation is a combination of 60° and 300°. The angle is the angle between the extension direction of the laser scanning trajectory and the length direction of the titanium-based amorphous alloy plate itself. After the multi-pass laser melting and solidification process, the periodic gradient heterostructure titanium-based amorphous alloy is obtained. The laser power of each single laser pass is 700-800 W, the scanning speed is 120-180 mm / s, and the center-to-center distance between adjacent laser passes is 0.8-1.2 mm.
[0036] In a specific implementation, a titanium-based amorphous alloy plate is subjected to multi-stage laser melting and solidification processing. A single-orientation design is used for the periodic gradient heterostructure, with the single orientation angle being 0°. The periodic gradient heterostructure formed by the titanium-based amorphous alloy plate in the depth and horizontal directions is as follows: Figure 1 As shown. From Figure 1As can be seen in (a), the titanium-based amorphous alloy plate is divided into three core regions from the surface to the interior: the first is the surface laser-melted amorphous pool region, which maintains a pure amorphous state because its cooling rate is higher than the critical cooling rate of the titanium-based amorphous alloy; the second is the middle heat-affected zone, where Zr2Ni and Ti2Ni crystalline phases precipitate on the amorphous matrix due to the heat conducted by the molten pool, and the size and density of the crystalline phases decrease gradually along the depth direction; the third is the bottom original matrix amorphous region, which is not affected by laser thermal action and maintains the as-cast amorphous structure. Figure 1 As can be seen in (b), the plane exhibits a periodic distribution pattern of alternating hard and soft regions: the hard region is the molten pool region formed by multiple laser melting and solidification, which has a low free volume concentration of amorphous phase and high hardness, corresponding to the coverage range of the laser scanning trajectory; the soft region is the original matrix region that has not been directly melted and solidified by the laser, which has a high free volume concentration of amorphous phase and low hardness, and is located between adjacent molten pools.
[0037] When stretching a titanium-based amorphous alloy plate along its own length, 0° corresponds to the arrangement direction of the hard and soft regions in the heterostructure (i.e., the extension direction of the laser scanning trajectory) being parallel to the stretching direction, while 90° corresponds to a perpendicular relationship between the two. These two angles constitute two extreme distribution orientations for orientation control. Specifically, at 0° orientation, the shear bands easily extend sequentially along the arrangement direction of the hard and soft structure after the alloy is stretched, and the stress transmission path is smooth. At 90° orientation, the heterostructure can form the most direct mechanical obstacle to the expansion of the shear bands, and the stress transmission is significantly restricted. These two angles can completely cover the scenarios of forward adaptation and reverse conflict between orientation and stress transmission.
[0038] The present invention will be further described below with reference to the accompanying drawings and specific embodiments, so that those skilled in the art can better understand and implement the present invention. However, the embodiments described are not intended to limit the present invention.
[0039] Unless otherwise specified, the experimental methods used in the following examples are conventional methods, and the materials and reagents used are commercially available.
[0040] Ti used in the following examples 33 Zr 30 Cu9Ni 5.3 Be 22.6 The titanium-based amorphous alloy plate was purchased from Panxing New Alloy Materials (Changzhou) Co., Ltd., and its dimensions are 100 mm × 50 mm × 2 mm.
[0041] Example 1
[0042] A laser melting and solidification method for preparing a periodically gradient heterostructure titanium-based amorphous alloy plate includes the following steps:
[0043] First, for Ti33 Zr 30 Cu9Ni 5.3 Be 22.6 The surface of the titanium-based amorphous alloy plate is polished with fine sandpaper to ensure uniform surface roughness. Then, it is ultrasonically cleaned with acetone and ethanol in sequence to thoroughly remove surface oil and impurities and ensure the cleanliness of the substrate surface. After cleaning, X-ray diffraction analysis is performed on the plate to confirm that the plate has a pure amorphous structure.
[0044] Pretreated Ti in an argon atmosphere 33 Zr 30 Cu9Ni 5.3 Be 22.6 A titanium-based amorphous alloy plate was subjected to multi-pass laser melting and solidification treatment with an argon flow rate of 5 L / min. The multi-pass lasers were arranged in parallel along the surface of the titanium-based amorphous alloy plate. The angle between the extension direction of the laser scanning trajectory and the length direction of the titanium-based amorphous alloy plate itself was 30°. The laser power of a single laser was 750 W, the scanning speed was 150 mm / s, and the center-to-center distance between adjacent lasers was 1 mm. Finally, a periodic gradient heterostructure titanium-based amorphous alloy plate was obtained.
[0045] Example 2
[0046] A laser melting and solidification preparation method for a periodic gradient heterostructure titanium-based amorphous alloy plate is basically the same as that in Example 1, except that the angle between the extension direction of the laser scanning trajectory and the length direction of the titanium-based amorphous alloy plate itself is 60°.
[0047] Example 3
[0048] A laser melting and solidification preparation method for a periodic gradient heterostructure titanium-based amorphous alloy plate is basically the same as that in Example 1, except that the angle between the extension direction of the laser scanning trajectory and the length direction of the titanium-based amorphous alloy plate itself is a combination of 60° and 300°.
[0049] Comparative Example 1
[0050] A laser melting and solidification preparation method for a periodic gradient heterostructure titanium-based amorphous alloy plate is basically the same as that in Example 1, except that the angle between the extension direction of the laser scanning trajectory and the length direction of the titanium-based amorphous alloy plate itself is 0°.
[0051] Comparative Example 2
[0052] A laser melting and solidification preparation method for a periodic gradient heterostructure titanium-based amorphous alloy plate is basically the same as that in Example 1, except that the angle between the extension direction of the laser scanning trajectory and the length direction of the titanium-based amorphous alloy plate itself is 90°.
[0053] Comparative Example 3
[0054] A laser melting and solidification preparation method for a periodic gradient heterostructure titanium-based amorphous alloy plate is basically the same as that in Example 1, except that the angle between the extension direction of the laser scanning trajectory and the length direction of the titanium-based amorphous alloy plate itself is a combination of 30° and 330°.
[0055] Comparison Example
[0056] First, for Ti 33 Zr 30 Cu9Ni 5.3 Be 22.6 The surface of the titanium-based amorphous alloy plate was polished with fine sandpaper to ensure uniform surface roughness. Subsequently, it was ultrasonically cleaned sequentially with acetone and ethanol to thoroughly remove surface oil and impurities, ensuring a clean substrate surface. After cleaning, X-ray diffraction analysis was performed to confirm that the plate has a pure amorphous structure. The Ti in this comparative example... 33 Zr 30 Cu9Ni 5.3 Be 22.6 Titanium-based amorphous alloy plates do not undergo subsequent laser melting and solidification treatment.
[0057] Test Example 1
[0058] Ti compared to the control example 33 Zr 30 Cu9Ni 5.3 Be 22.6 Micro-area X-ray diffraction (XRD) tests were performed on titanium-based amorphous alloy plates, periodic gradient heterostructure titanium-based amorphous alloy plates prepared in Examples 1-3 and Comparative Examples 1-3. The X-ray source used for the test was a monochromatic Cu target K-ray. The scanning range was set to 20°-90°, the scanning speed was 5° / min, the instrument operating voltage and operating current were 40 kV and 40 mA, respectively, and the micro-area measurement range was 300 μm × 300 μm.
[0059] Figure 2 Ti, as a control example 33 Zr 30 Cu9Ni 5.3 Be 22.6 XRD patterns of titanium-based amorphous alloy plates, periodically gradient heterostructure titanium-based amorphous alloy plates prepared in Examples 1-3 and Comparative Examples 1-3, from... Figure 2 As can be seen, after laser melting and solidification treatment, the titanium-based amorphous alloy plate exhibits obvious amorphous diffuse scattering diffraction peaks at 2θ=38° at different positions of its cross-section, and no significant crystallization characteristic peaks are detected. This indicates that laser melting and solidification treatment does not induce alloy crystallization, and the treated titanium-based amorphous alloy plate can still maintain a good amorphous heterostructure.
[0060] Test Example 2
[0061] Ti compared to the control example 33 Zr 30 Cu9Ni 5.3 Be 22.6 Mechanical properties of titanium-based amorphous alloy plates, periodically gradient heterostructure titanium-based amorphous alloy plates prepared in Examples 1-3 and Comparative Examples 1-3 were tested. The tensile properties were tested by machining the titanium-based amorphous alloy plates into standard tensile specimens using wire electrical discharge machining (EDM), according to GB / T 228.1-2021. The surfaces of the tensile specimens were then polished and ultrasonically cleaned sequentially with acetone and anhydrous ethanol to thoroughly remove impurities and oil. After drying, the specimens were placed in a tensile testing machine for testing, with the tensile rate set at 0.18 mm / min. Figure 3 This is a schematic diagram showing the distribution orientation of the periodic gradient heterostructures in Examples 1-3 and Comparative Examples 1-3, with the stretching direction as shown in Table 1. The test results are shown in Table 1 and... Figure 4 As shown:
[0062] Table 1. Data on Elongation at Break and Fracture Strength
[0063]
[0064] Figure 4 For Ti 33 Zr 30 Cu9Ni 5.3 Be 22.6 Stress-strain curves of titanium-based amorphous alloy plates, periodically gradient heterostructure titanium-based amorphous alloy plates prepared in Examples 1-3 and Comparative Examples 1-3. Figure 4 As shown in Table 1, Ti that has not undergone laser melting treatment... 33 Zr 30 Cu9Ni 5.3 Be 22.6 The titanium-based amorphous alloy plate exhibited a fracture strength of 1162 MPa and an elongation of 7.76%. In samples treated with unidirectional laser melting, the elongation gradually increased with increasing orientation angle, while the fracture strength initially increased and then decreased. The titanium-based amorphous alloy plate with an orientation angle of 60° (Example 2) showed the best tensile performance, with a fracture strength of 1469 MPa and an elongation of 9.33%, representing an increase of approximately 26% in fracture strength and approximately 20% in elongation compared to the untreated titanium-based amorphous alloy plate. Among samples treated with bidirectional laser melting, the combination of 60° and 300° orientations demonstrated superior overall tensile properties.
[0065] Obviously, the above embodiments of the present invention are merely examples for clearly illustrating the present invention, and are not intended to limit the implementation of the present invention. Those skilled in the art should understand that other variations or modifications can be made based on the above description. It is neither necessary nor possible to exhaustively describe all embodiments here. Any modifications, equivalent substitutions, and improvements made within the spirit and principles of the present invention should be included within the scope of protection of the claims of the present invention.
Claims
1. A laser melting and solidification method for preparing a periodically gradient heterostructure titanium-based amorphous alloy, characterized in that, Includes the following steps: A multi-pass laser melting and solidification process is performed on a titanium-based amorphous alloy. Each laser pass is arranged parallel to the surface of the titanium-based amorphous alloy, employing a single-pass sequential melting and solidification method with consistent process parameters for each laser pass. During this multi-pass laser melting and solidification process, a periodic gradient heterostructure is designed for distribution and orientation. This distribution and orientation includes single orientation and composite orientation. The angle of the single orientation is 30° or 60°, and the angle combination of the composite orientation is a combination of 60° and 300°. The angle is the angle between the extension direction of the laser scanning trajectory and the length direction of the titanium-based amorphous alloy plate itself. After the multi-pass laser melting and solidification process, the periodic gradient heterostructure titanium-based amorphous alloy is obtained. The laser power of each single laser pass is 700-800 W, the scanning speed is 120-180 mm / s, and the center-to-center distance between adjacent laser passes is 0.8-1.2 mm.
2. The laser melting and solidification preparation method according to claim 1, characterized in that, The titanium-based amorphous alloy is a titanium-based amorphous alloy plate.
3. The laser melting and solidification preparation method according to claim 2, characterized in that, The titanium-based amorphous alloy is Ti 33 Zr 30 Cu9Ni 5.3 Be 22.6 Titanium-based amorphous alloy plate.
4. The laser melting and solidification preparation method according to claim 2, characterized in that, The thickness of the titanium-based amorphous alloy plate is 1.5-2.5 mm.
5. The laser melting and solidification preparation method according to claim 1, characterized in that, Before performing multiple laser melting and solidification processes, a pretreatment step is also included for the titanium-based amorphous alloy; the pretreatment includes grinding and cleaning steps.
6. The laser melting and solidification preparation method according to claim 5, characterized in that, The pretreatment includes sequentially performing fine sandpaper polishing, acetone ultrasonic cleaning, and ethanol ultrasonic cleaning.
7. The laser melting and solidification preparation method according to claim 1, characterized in that, The wavelength of the single-channel laser is 1065-1080 nm.
8. The laser melting and solidification preparation method according to claim 1, characterized in that, The spot diameter of the single-channel laser is 1.5-2.5 mm.
9. The laser melting and solidification preparation method according to claim 1, characterized in that, The multi-stage laser melting and solidification process is carried out in an argon atmosphere with an argon flow rate of 4-6 L / min.
10. A periodic gradient heterostructure titanium-based amorphous alloy prepared by the laser melting and solidification method according to any one of claims 1-9.