High-performance low-alloying zinc alloy plate foil, preparation method and application

Abstract

The invention belongs to the technical field of zinc alloy preparation, and particularly relates to a high-performance low-alloying zinc alloy plate foil and a preparation method and application thereof.The high-performance low-alloying zinc alloy plate foil is prepared from, by weight, 0.4-0.8% of Cu, 0.01-0.05% of Mg and the balance Zn; the preparation method of the high-performance low-alloying zinc alloy plate foil comprises the steps that a zinc alloy cast ingot is sequentially subjected to homogenization treatment, forging and rolling, and the high-performance low-alloying zinc alloy plate foil is obtained; rolling is carried out for multiple times, annealing treatment is carried out between every two times of rolling, the rolling temperature ranges from 150 DEG C to 200 DEG C, the rolling reduction of single-pass rolling is not larger than 0.5 mm, and the annealing time is not larger than 30 min; on the basis of keeping relatively good strength, the high-ductility high-strength aluminum alloy has relatively high ductility.

Description

Technical Field

[0001] This invention belongs to the field of zinc alloy preparation technology, specifically relating to a high-performance low-alloy zinc alloy plate and foil, its preparation method, and its application. Background Technology

[0002] Biodegradable metallic materials offer significant advantages in fields such as orthopedics and cardiovascular medicine because they do not require secondary surgery for removal. Zinc alloys, with their excellent biocompatibility and controllable degradation rate, are considered the third generation of biodegradable metals after magnesium and iron.

[0003] Currently, the mechanical properties of zinc alloys are mainly improved through alloying and subsequent plastic deformation. Developed zinc alloys mainly include Zn-Mg, Zn-Li, Zn-Mn, and Zn-Cu systems, as well as various ternary and multi-component alloy systems based on these alloys. Considering the unique aging phenomenon of zinc alloys, elements with high solid solubility should be prioritized in alloying design to achieve solid solution strengthening. Since the limiting solid solubility of Cu in zinc is approximately 2.75%, Cu, with its excellent antibacterial properties, is preferred as the primary alloying element.

[0004] Existing zinc alloy materials still have shortcomings in terms of performance and preparation: On the one hand, to improve mechanical properties, some zinc alloys adopt high alloying designs, leading to increased material costs, and excessive alloying elements may adversely affect biocompatibility; on the other hand, in the preparation of plates / foils, traditional processes struggle to balance high strength, high plasticity, and processability, especially for foils with a thickness of less than 0.2 mm, which often face problems such as high processing difficulty and unstable mechanical properties, making it difficult to meet the stringent requirements of high-end medical devices such as bone plates and dental repair membranes. Zinc belongs to the hexagonal close-packed (HCP) crystal structure with a relatively small number of slip systems. Rolling, as a traditional plate / foil forming process, typically uses large reductions and low rolling temperatures. Traditional preparation methods cause the continuous accumulation of basal-oriented grains, eventually forming a strong basal texture. While this texture can improve the strength of certain directions to some extent, it also leads to significant anisotropy in zinc alloy plates, which is detrimental to subsequent processing and the improvement of overall mechanical properties.

[0005] Patent application AU2020102744A4 discloses a high-performance biodegradable Zn-Cu-Li-X alloy and its preparation and application methods. The chemical composition of the alloy is as follows: Cu 0.1~2.75wt%, Li 0.1~1.5wt%, X is at least one selected from Mg, Ca, Sr, Mn, Fe, Ag, Co, Cr, Ti, Sn, Si, Se, and Ge; Mg 0.01~9.9wt%, Ca 0.01~5.8wt%, Sr 0.01~9.5wt%, Mn 0.01~8.5wt%, Fe 0.01~6.1wt%, Ag 0.01~10.5wt%, Co 0.01~6.4wt%, Cr 0.01~4.4wt%, Ti 0.01~ 4.8 wt%, Sn 0.01~5 wt%, Si 0.01~5 wt%, Se 0.01~5 wt%, Ge 0.01~5 wt%, with the balance being Zn. However, its elongation is generally low. Summary of the Invention

[0006] The technical problem to be solved by the present invention is to provide a high-performance low-alloy zinc alloy plate and foil, a preparation method and an application, which has a high elongation while maintaining good strength.

[0007] This invention provides a high-performance low-alloy zinc alloy sheet and foil, comprising the following components by weight percentage: Cu 0.4-0.8%, Mg 0.01-0.05%, and the balance being Zn; The preparation method of the high-performance low-alloy zinc alloy plate and foil is as follows: the zinc alloy ingot is subjected to homogenization treatment, forging and rolling in sequence to obtain the high-performance low-alloy zinc alloy plate and foil. The rolling process is performed in multiple passes, with annealing between each pass. The rolling temperature is 150–200°C, the reduction per pass is no more than 0.5 mm, and the annealing time is no more than 30 min.

[0008] The zinc alloy sheet and foil of the present invention includes a sheet and a foil, wherein the thickness of the sheet is generally less than 1 mm and the thickness of the foil is generally less than 0.2 mm.

[0009] Preferably, it also includes Ca and / or Sr, wherein the weight percentage of Ca and / or Sr is 0.08 to 0.15%.

[0010] Preferably, the weight percentage of Ca and / or Sr is 0.1% to 0.15%.

[0011] Preferably, the composition includes the following components by weight percentage: Cu 0.5-0.7%, Mg 0.02-0.03%, Ca 0.05-0.1%, Sr 0.05-0.1%, with the balance being Zn.

[0012] Preferably, the weight ratio of Ca to Sr is 1:1 to 2.

[0013] This invention provides a method for preparing the high-performance low-alloy zinc alloy plate and foil material, wherein the zinc alloy ingot is subjected to homogenization treatment, forging, and rolling in sequence to obtain the high-performance low-alloy zinc alloy plate and foil material. The rolling process is performed in multiple passes, with annealing between each pass. The rolling temperature is 180–220°C, the reduction per pass is no more than 0.5 mm, and the annealing time is no more than 30 min.

[0014] Preferably, the homogenization treatment is performed at a temperature of 280–300°C for 6–12 hours.

[0015] Preferably, the rolling temperature is 180-200°C, and the rolling is performed in multiple passes, each pass including multiple single-pass rolling, with adjacent rolling passes having different directions.

[0016] Preferably, the zinc alloy ingot is prepared by melting the components, heating it to 520-550 °C under inert gas protection, holding it at that temperature for 3-5 min, then cooling it to 480-500 °C, then heating it again to 550-570 °C, and then casting it.

[0017] The forging process of this invention can forge zinc alloy ingots into pre-rolled plates of predetermined thickness and width.

[0018] This invention provides an application of the high-performance low-alloy zinc alloy sheet and foil, which is used to manufacture medical devices implanted in the body.

[0019] The beneficial effects of this invention are that the zinc alloy sheet of this invention has a bi-level heterogeneous structure in terms of grain orientation and grain size, formed by alternating bimodal orientation heterogeneous structures and fine-grained regions formed by dynamic recrystallization and coarse-grained regions due to residual deformation. Based on the heterogeneous structure enhancement effect brought about by the grain size and grain orientation structure, this invention provides the alloy with high strength and toughness, anti-aging ability, and controllable degradation. The zinc alloy foil of this invention has high tensile strength and elongation at break. Under specific conditions, the elongation at break of the zinc alloy sheet and foil of this invention can reach ≥100%, while ensuring a tensile strength ≥300 MPa.

[0020] The zinc alloy plate and foil of the present invention have excellent antibacterial properties, degradation properties and osteogenic properties. The mechanical properties change by ≤5% within six months of storage at room temperature. The plate can be used in bone plates for internal fixation systems, while the foil can be used in products such as oral repair membranes. It has broad market prospects and good medical value.

[0021] This invention introduces high-density twins in the early stages of forging. As the interaction of twin dislocations intensifies, non-basal plane slip within the twins is activated. Furthermore, a bimodal orientation texture and a bilevel heterogeneous grain size structure are successfully prepared through anisotropic rolling, achieving a balance between alloy strength and toughness, and exhibiting more sustained strain hardening capability under high strain. Simultaneously, by adding alkaline earth metal ternary elements (magnesium (Mg), calcium (Ca), and strontium (Sr)) to the Zn-Cu alloy base, a superplastic zinc alloy is successfully prepared through forging and rolling.

[0022] The zinc alloy of this invention forms a CuZn4 phase with an area fraction of no more than 5%; the trace magnesium element is added entirely in the form of solute atoms. Within the compositional range defined by this invention, the Zn-Cu-(Mg / Ca / Sr) alloy microstructure, in addition to containing an η-Zn matrix and a bulk ε-CuZn4 phase, also contains at least Mg2Zn. 11 Phase, CaZn 13 Phase and SrZn 13 At least one of the phases. During the forging and rolling process of this invention, the microstructure of the zinc alloy mainly undergoes the following changes: 1) In the early stage of forging, the Zn-Cu-(Mg / Ca / Sr) alloy with excellent thermal stability forms high-density twins to adapt to deformation and achieve the effect of dividing the original parent crystal and refining the grains.

[0023] 2) As the forging deformation increases, the interaction between twins and dislocations intensifies, which is conducive to the generation of non-basal plane slip. Due to the twin-induced dynamic recrystallization and its promoting effect on continuous induced dynamic recrystallization, subgrains can be formed in the twins and dislocation arrays in the deformation zone. At the same time, subgrains can also be formed at twin intersections, including small-angle grain boundaries at twin boundaries.

[0024] 3) During the rolling process, a bimodal orientation texture and a bilevel heterogeneous grain size structure were successfully prepared through anisotropic rolling, achieving a balance between the alloy's strength and toughness, and exhibiting a more sustained strain hardening capability under large strain. Simultaneously, by adding an alkaline earth metal tertiary element to the Zn-Cu alloy, a superplastic Zn alloy was successfully prepared through forging and rolling.

[0025] In this invention, high-density twins are introduced, and the heterogeneous grain size structure is synergistically controlled through twin-induced dynamic recrystallization and continuous-induced dynamic recrystallization. Simultaneously, a bimodal texture is successfully prepared through anisotropic rolling, overcoming the adverse effects of strong basal plane texture in traditional rolling processes. In particular, the activation of non-basal plane slip promotes a more uniform deformation process, coordinating the strain along the c-axis of the grains and reducing anisotropy. Therefore, by dual heterogeneous induction to enhance and control work hardening behavior, a more sustained work hardening capability is achieved over a large strain range.

[0026] The total content of alloying elements in the zinc alloy of this invention does not exceed 0.8%. Among them, Cu, with its excellent antibacterial properties, is beneficial to improving its mechanical properties and regulating the degradation rate. Further microalloying, including alkaline earth metals (Mg, Ca, Sr) as tertiary elements, enhances mechanical properties while promoting bone tissue repair and regeneration. This is particularly suitable for the efficient preparation of bone implant materials such as high-strength biodegradable bone plates and highly plastic bone-guided regeneration membranes. Attached Figure Description

[0027] Figure 1 The SEM microstructure of the Zn-0.6Cu-0.025Mg alloy in Example 1 of this invention shows an average grain size of approximately 1.9 μm in the zinc matrix, exhibiting a bimodal texture with a maximum texture intensity of 13.9. Figure 1 (a) is a SEM tissue. Figure 1 (b) are polar diagrams and inverse polar diagrams.

[0028] Figure 2 The SEM microstructure of the Zn-0.6Cu-0.025Mg alloy in Comparative Example 2 shows an average grain size of approximately 36.3 μm in the zinc matrix, high-density twins, and a bimodal texture with a maximum texture intensity of 6.0. Figure 2 (a) is a SEM tissue. Figure 2 (b) are polar diagrams and inverse polar diagrams.

[0029] Figure 3 The SEM microstructure of pure Zn in Comparative Example 5 shows an average grain size of approximately 67.2 μm in the zinc matrix, with a small number of twins present and a maximum texture intensity of 6.7. Figure 3 (a) is a SEM tissue. Figure 3 (b) are polar diagrams and inverse polar diagrams. Detailed Implementation

[0030] To make the objectives, technical solutions, and advantages of this invention clearer, the invention will be described in detail below with reference to some specific embodiments. The specific embodiments described herein are only for explaining the invention and are not intended to limit the invention.

[0031] Example 1 A biodegradable Zn-Cu-Mg alloy for medical use, wherein the mass fraction of elements is Cu: 0.6%, Mg: 0.025%, and the balance is Zn.

[0032] The preparation method is as follows: (1) Batching: The raw materials are prepared according to the alloy composition design. The raw materials include pure zinc ingots, zinc-copper master alloy, zinc-magnesium master alloy, zinc-calcium master alloy and zinc-strontium master alloy.

[0033] (2) Smelting: Pure zinc ingots, zinc-copper master alloys and zinc-magnesium master alloys are smelted under an inert atmosphere to obtain zinc alloy ingots.

[0034] Specifically, a graphite crucible with a melting point above 3000 ℃ is used, and the vacuum degree of melting is ≤1×10⁻⁶. -3 Pa; The melting process is carried out in two steps. First, the temperature is raised to 530 °C and held for 4 minutes. Then, the temperature is lowered to 500 °C and then rapidly raised to 550 °C again while electromagnetic stirring is performed at a frequency of 1000 Hz. After the melt temperature reaches 550 °C, it is quickly poured into a graphite mold. The temperature of the mold is controlled at 220 °C.

[0035] (3) Homogenization treatment: The above zinc alloy ingot is subjected to homogenization treatment at a temperature of 300 ℃ and a holding time of 12 h.

[0036] (4) Forging: A 50 mm diameter bar is machined from the homogenized zinc alloy ingot. The zinc alloy bar is then forged repeatedly to form a 9.5 mm thick sheet. A 0.5 mm skin layer is milled on each side to obtain a pre-rolled sheet with a thickness of 8.5 mm and a width of 65 mm.

[0037] (5) Rolling: The pre-rolled sheet is vacuum heated to 180°C and held for 0.2 hours. After multiple rolling passes, the width of the pre-rolled sheet is widened to 110 mm and the thickness is reduced to 5.5 mm, with a single-pass reduction of ≤0.5 mm (pass deformation of 5.88-9.1%). Subsequently, it is subjected to intermediate annealing at 180°C for 0.2 hours. After annealing and cooling, it is subjected to reversing rolling to further reduce the thickness to 1.0 mm, with a single-pass reduction of ≤0.3 mm (pass deformation of 5.45-30%).

[0038] The zinc alloy sheet has a bi-level heterogeneous structure with different grain orientations and grain sizes, with a maximum texture strength of 13.9 and an average grain size of 1.9 μm.

[0039] Because the total alloying element content of this zinc alloy is less than 0.8%, the solid solution strengthening effect of copper in the zinc matrix is ​​fully utilized, while the addition of trace amounts of magnesium further significantly improves the mechanical properties. The increase in uniform elongation is due to work hardening caused by the mismatch in deformation compatibility between coarse and fine grains in the heterostructure, resulting in a more sustained strain hardening capacity during tensile loading. Therefore, under the heterogeneous induced strengthening effect of the bi-level heterostructure of this invention, the zinc alloy achieves a combination of high strength and toughness and high work hardening rate, effectively preventing the zinc alloy implant from fracturing due to excessive deformation in local locations. In addition, the solid solution of a certain amount of high-melting-point Cu and trace amounts of Mg in the low-melting-point zinc matrix significantly improves the thermal stability of the Zn matrix, thereby greatly enhancing the anti-aging properties of the Zn alloy.

[0040] Example 2 The difference between Example 2 and Example 1 is as follows: In step (5), during the rolling process, the sheet material thinned to 1.0 mm is subjected to intermediate annealing at 180°C for 0.2 hours. After annealing and cooling, it is further thinned to 0.1 mm by rolling.

[0041] Everything else is the same as in Example 1.

[0042] This zinc alloy foil has a bi-level heterogeneous structure with different grain orientations and grain sizes, a maximum texture strength of 12.4, and an average grain size of 1.6 μm.

[0043] Example 3 The difference between Example 3 and Example 1 is as follows: In step (5), during the rolling process, the sheet material thinned to 5.5 mm is subjected to intermediate annealing at 180°C for 0.3 hours. After annealing and cooling, it is subjected to reversing rolling to further thin it to 1.0 mm.

[0044] The other steps are the same as in Example 1.

[0045] The zinc alloy sheet has a bi-level heterogeneous structure with different grain orientations and grain sizes, with a maximum texture strength of 13.7 and an average grain size of 1.8 μm.

[0046] Example 4 The difference between Example 4 and Example 1 is that the mass fraction of each element in the alloy is Cu: 0.6%, Mg: 0.025%, Ca: 0.1%, and the balance is Zn.

[0047] The other steps are the same as in Specific Implementation Example 1.

[0048] This superplastic zinc alloy sheet has a bi-level heterogeneous structure with different grain orientations and grain sizes, a maximum texture strength of 9.1, and an average grain size of 1.7 μm.

[0049] Example 5 Compared with Example 1, Example 5 differs in that the mass fraction of each element in the alloy is Cu: 0.6%, Mg: 0.025%, Sr: 0.1%, with the balance being Zn.

[0050] The other steps are the same as in Specific Implementation Example 1.

[0051] This superplastic zinc alloy sheet has a bi-level heterogeneous structure with different grain orientations and grain sizes, a maximum texture strength of 8.2, and an average grain size of 1.3 μm.

[0052] Example 6 Compared with Example 1, Example 6 differs in that the mass fraction of each element in the alloy is Cu: 0.6%, Mg: 0.025%, Ca: 0.05%, Sr: 0.05%, with the balance being Zn.

[0053] The other steps are the same as in Specific Implementation Example 1.

[0054] This superplastic zinc alloy sheet has a bi-level heterogeneous structure with different grain orientations and grain sizes, a maximum texture strength of 6.9, and an average grain size of 1.1 μm.

[0055] Example 7 Compared with Example 1, Example 7 differs in that the mass fraction of each element in the alloy is Cu: 0.6%, Mg: 0.025%, Ca: 0.05%, Sr: 0.1%, with the balance being Zn.

[0056] The other steps are the same as in Specific Implementation Example 1.

[0057] This superplastic zinc alloy sheet has a bi-level heterogeneous structure with different grain orientations and grain sizes, a maximum texture strength of 8.2, and an average grain size of 1.3 μm.

[0058] Comparative Example 1 Compared with Example 1, the difference is that in step (5) during the rolling process, the pre-rolled plate in Comparative Example 1 does not need to be rolled in the opposite direction, that is, it is rolled directly along the long side of the wide pre-rolled plate and its thickness is reduced to 1.0 mm.

[0059] The other steps are the same as in Specific Implementation Example 1.

[0060] This superplastic zinc alloy sheet has a bi-level heterogeneous structure with different grain orientations and grain sizes, a maximum texture strength of 17.3, and an average grain size of 1.4 μm.

[0061] Comparative Example 2 Compared with Example 1, Comparative Example 2 differs in that: during the rolling process in step (5), the sheet material thinned to 1.0 mm is subjected to intermediate annealing at 180°C for 2 hours. After annealing and cooling, it is further thinned to 0.03 mm by rolling.

[0062] The other steps are the same as in Specific Implementation Example 1.

[0063] This superplastic zinc alloy foil has a high-density twinning and bimodal orientation heterostructure, with a maximum texture strength of 6.0 and an average grain size of 36.3 μm.

[0064] Comparative Example 3 Compared with Example 1, Comparative Example 3 differs in that the mass fraction of each element in the alloy is Ca: 0.15%, with the balance being Zn.

[0065] The other steps are the same as in Specific Implementation Example 1.

[0066] This superplastic zinc alloy sheet has a bi-level heterogeneous structure with different grain orientations and grain sizes, a maximum texture strength of 11.3, and an average grain size of 2.4 μm.

[0067] Comparative Example 4 Compared with Example 1, Comparative Example 4 differs in that the mass fraction of each element in the alloy is Sr: 0.6%, with the balance being Zn.

[0068] The other steps are the same as in Specific Implementation Example 1.

[0069] This superplastic zinc alloy sheet has a bi-level heterogeneous structure with different grain orientations and grain sizes, a maximum texture strength of 11.3, and an average grain size of 0.9 μm.

[0070] Comparative Example 5 Compared with Example 1, Comparative Example 5 is different in that it is pure Zn with no alloying elements added.

[0071] The other steps are the same as in Specific Implementation Example 1.

[0072] The pure Zn plate exhibits coarse equiaxed crystals with a maximum texture strength of 6.7 and an average grain size of 67.2 μm.

[0073] By adjusting the mass of each element in the Zn-Cu-Mg-Ca-Sr alloy, Comparative Examples 6-10 were obtained, with other aspects remaining the same as in Example 1. The properties of each example and comparative example were measured, and the mechanical properties of the zinc alloys are shown in Table 1.

[0074] Table 1 Comparison of mechanical properties of zinc alloys

[0075] Tensile strength (UTS) is measured in MPa, and elongation at break (TE) is measured in MPa.

[0076] As shown in Table 1, the low-alloyed Zn0.6Cu0.025Mg alloy sheet and foil exhibit an excellent combination of strength and toughness, maintaining a strength above 370 MPa and an elongation at break exceeding 52%. Maintaining a Cu content of 0.6% / Mg of 0.025%, the addition of trace amounts of Sr-Ca composite material enables the zinc alloy to achieve "medium-high strength (≈300 MPa) + ultra-high elongation (>50%)", significantly superior to the control group with no or excessive addition. The amount of Ca and / or Sr added in this invention is subject to requirements; the total content must be between 0.1% and 0.5%, exceeding or falling below this range will significantly reduce the improvement in elongation at break. Simultaneously, short-time annealing (annealing time <0.5 h) is beneficial for improving work hardening ability, resulting in higher strength and plasticity in the zinc alloy. In contrast, in Control Example 2, where the annealing time was greater than 1 h, abnormal grain growth led to a significant decrease in plasticity. Furthermore, bimodal orientation texture and a bilevel heterogeneous structure with different grain sizes were successfully prepared by anisotropic rolling, achieving efficient coordination of alloy strength and toughness, and exhibiting more sustained strain hardening capability under large strain.

[0077] As can be seen from Comparative Examples 6-10, when the Cu content is excessive (e.g., Cu ≥ 2%), the tensile strength decreases significantly. Copper is a heavy metal and its content should not be too high in implanted medical devices. Based on Zn-Cu-Mg low alloying, when the total addition of alkaline earth metal elements Ca and Sr exceeds 0.15%, the strength decreases significantly.

[0078] like Figure 1 As shown, the SEM microstructure of the Zn-0.6Cu-0.025Mg alloy in Example 1 of this invention is shown. The average grain size of the zinc matrix is ​​about 1.9 μm, and it exhibits a bimodal texture with a maximum texture intensity of 13.9.

[0079] like Figure 2 As shown, the SEM microstructure of the Zn-0.6Cu-0.025Mg alloy in Comparative Example 2 is shown. The average grain size of the zinc matrix is ​​about 36.3 μm, with high-density twins and a bimodal texture. The maximum texture intensity is 6.0.

[0080] like Figure 3 As shown, the SEM structure of pure Zn in Comparative Example 5 is as follows: the average grain size of the zinc matrix is ​​about 67.2 μm, a small number of twins are present, and the maximum texture intensity is 6.7.

[0081] It can be seen that the addition of Cu, an element with high solid solubility, in this invention is beneficial to improving its mechanical properties. Further, microalloying with alkaline earth metals (Mg, Ca, Sr) as a tertiary element enhances mechanical properties while promoting bone tissue repair and regeneration, and exhibits good biocompatibility. The aforementioned low-alloyed zinc alloy plates and foils possess excellent antibacterial properties, degradation resistance, and osteogenic capacity, with mechanical property changes of ≤5% within six months of room temperature storage. The plates can be used in bone plates for internal fixation systems, while the foils can be applied to products such as dental repair membranes, demonstrating broad market prospects and significant medical value.

[0082] Those skilled in the art should understand that the discussion of any of the above embodiments is merely exemplary and is not intended to imply that the scope of protection of this application is limited to these examples; within the framework of this application, the technical features of the above embodiments or different embodiments can also be combined, the steps can be implemented in any order, and there are many other variations of different aspects of one or more embodiments of this application as described above, which are not provided in detail for the sake of brevity.

[0083] One or more embodiments in this application are intended to cover all such substitutions, modifications, and variations that fall within the broad scope of this application. Therefore, any omissions, modifications, equivalent substitutions, improvements, etc., made within the spirit and principles of one or more embodiments in this application should be included within the protection scope of this application.

Claims

1. A high-performance low-alloy zinc alloy sheet / foil, characterized in that, It includes the following components by weight percentage: Cu 0.4–0.8%, Mg 0.01–0.05%, with the balance being Zn; The preparation method of the high-performance low-alloy zinc alloy plate and foil is as follows: the zinc alloy ingot is subjected to homogenization treatment, forging and rolling in sequence to obtain the high-performance low-alloy zinc alloy plate and foil. The rolling process is performed in multiple passes, with annealing between each pass. The rolling temperature is 150–200°C, the reduction per pass is no more than 0.5 mm, and the annealing time is no more than 30 min.

2. The high-performance low-alloy zinc alloy sheet and foil as described in claim 1, characterized in that, It also includes Ca and / or Sr, with a weight percentage of Ca and / or Sr of 0.08 to 0.15%.

3. The high-performance low-alloy zinc alloy sheet and foil as described in claim 2, characterized in that, The weight percentage of Ca and / or Sr is 0.1% to 0.15%.

4. The high-performance low-alloy zinc alloy sheet and foil as described in claim 2, characterized in that, It includes the following components by weight percentage: Cu 0.5-0.7%, Mg 0.02-0.03%, Ca 0.05-0.1%, Sr 0.05-0.1%, with the balance being Zn.

5. The high-performance low-alloy zinc alloy sheet and foil as described in claim 2, characterized in that, The weight ratio of Ca to Sr is 1:1 to 2.

6. A method for preparing high-performance low-alloy zinc alloy sheet / foil as described in any one of claims 1-5, characterized in that, The zinc alloy ingots are sequentially homogenized, forged, and rolled to obtain high-performance low-alloy zinc alloy sheet and foil. The rolling process is performed in multiple passes, with annealing between each pass. The rolling temperature is 180–220°C, the reduction per pass is no more than 0.5 mm, and the annealing time is no more than 30 min.

7. The preparation method according to claim 6, characterized in that, The homogenization process is carried out at a temperature of 280–300°C for 6–12 hours.

8. The preparation method according to claim 6, characterized in that, The rolling temperature is 180-200℃, and the rolling is performed in multiple stages, with each rolling stage including multiple single-pass rolling, and adjacent rolling stages having different directions.

9. The preparation method according to claim 6, characterized in that, The zinc alloy ingot is prepared by melting the components, heating it to 520-550 °C under inert gas protection, holding it at that temperature for 3-5 minutes, then cooling it to 480-500 °C, then heating it again to 550-570 °C, and then casting it.

10. An application of the high-performance low-alloy zinc alloy sheet / foil as described in any one of claims 1-5, characterized in that, The high-performance low-alloy zinc alloy sheet and foil are used to manufacture medical devices that can be implanted in the body.

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