CN113733685B - Light high-strength Mg-Al-Ta composite metal plate and rolling forming method thereof - Google Patents
Light high-strength Mg-Al-Ta composite metal plate and rolling forming method thereof Download PDFInfo
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- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
- B32B15/017—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of aluminium or an aluminium alloy, another layer being formed of an alloy based on a non ferrous metal other than aluminium
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- B32B38/00—Ancillary operations in connection with laminating processes
- B32B38/0012—Mechanical treatment, e.g. roughening, deforming, stretching
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B38/00—Ancillary operations in connection with laminating processes
- B32B38/0036—Heat treatment
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
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- C—CHEMISTRY; METALLURGY
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/06—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of magnesium or alloys based thereon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
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- B—PERFORMING OPERATIONS; TRANSPORTING
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- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B38/00—Ancillary operations in connection with laminating processes
- B32B38/0036—Heat treatment
- B32B2038/0048—Annealing, relaxing
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B2307/00—Properties of the layers or laminate
- B32B2307/70—Other properties
- B32B2307/718—Weight, e.g. weight per square meter
Abstract
The embodiment of the invention provides a light high-strength Mg-Al-Ta composite metal plate and a rolling forming method of the composite metal plate.
Description
Technical Field
The invention relates to the technical field of metal material processing, in particular to a light high-strength Mg-Al-Ta composite metal plate and a rolling forming method thereof.
Background
The high-speed development of deep space exploration technology requires more and more severe materials to carry out space activities such as lunar exploration, mars exploration, solar outside system exploration and the like, and the detector faces very strong electromagnetic environments such as star radiation, solar wind, cosmic background radiation and the like, wherein the impact of high-energy particles on the service life and service life of spacecraft equipment is very large, and the detection performance of effective load can be even seriously deteriorated while the service life of the equipment is reduced. The deep space exploration of the stars in various countries takes the protection of high-energy particles as a key technology of structural design. Based on the requirements of the spacecraft emission and specific service environment on weight reduction, stability, radiation protection and the like, the light metal alloy with excellent electromagnetic shielding property is an important way for improving the performance of the detector, wherein the most important way is how to manufacture high-performance metal parts industrially with low cost.
At present, related detection structural members abroad are mostly manufactured by heavy metals with higher density. The influence of strong magnetic fields and high-energy particles on the electronic equipment is shielded by tough reflection, scattering and the like of heavy metals. For example, the shielding structural member is made of titanium alloy in the United states and pure tantalum metal in Europe, the weight of the detector structural member is greatly increased while the colored shielding is exerted, and the weight of the whole structure is not less than 180kg. The magnesium alloy is the lightest metal structural material, has high specific strength, excellent formability and low manufacturing cost, and is an important light metal material in the aerospace field, but has poor electromagnetic shielding performance. In order to optimize the overall performance of the spacecraft, the antimagnetic and high-energy particle bombardment performance of the material is optimized from the perspective of bimetal compounding, so that the magnesium/tantalum metal which ensures excellent radiation resistance and simultaneously reduces the weight of the structural member is manufactured.
However, for both light Mg alloy and pure Ta materials, the melting points of the two materials differ by 2300 ℃ (the melting point of tantalum is about 2995 ℃ and the melting point of magnesium is about 650 ℃), and the lattice structures are different (tantalum is BCC or magnesium HCP), so that the problems of interface uncombination, poor bonding and the like caused by interface deformation, unmatched thermophysical properties and the like in the cumulative rolling process are very easy to occur. Moreover, the mutual solubility of the two elements is very small (< 0.1%wt), as shown in the binary phase diagram of Mg-Al-Ta shown in figure 1, no diffusion between the elements can occur no matter what proportion is adopted between the two elements of magnesium and tantalum below 650 ℃, so that pure Mg and Ta can not form a metallurgical bonding interface with a certain depth, and the two elements all cause the technical bottleneck of room temperature roll forming of the Mg/Ta composite plate. Therefore, the patent provides a novel differential hot rolling process for adding the magnesium/tantalum composite plate with the pure aluminum interlayer, so that the magnesium/tantalum composite plate can be effectively combined, and meanwhile, the magnesium/tantalum composite plate has excellent strength.
At present, in the aspect of Mg/Ta rolling forming, as disclosed in Chinese patent CN112742870A, a preparation method of a heterogeneous shielding type magnesium-tantalum multilayer composite board is characterized in that during Mg/Ta rolling forming, hot rolling forming of magnesium alloy and pure tantalum is carried out in a sheath mode, and although a formed Mg/Ta composite board can be obtained, the service performance, particularly the strength performance, is not very ideal, and the engineering production efficiency of the composite board is influenced by a hot rolling forming process.
Disclosure of Invention
The invention aims to solve the problems and provides a light high-strength Mg-Al-Ta composite metal plate and a rolling forming method thereof. The magnesium and tantalum metal are connected through the special interlayer light metal by adding the rolling interlayer, the plate has the advantages of light weight, high strength, mechanical and metallurgical bonding interface and the like, and when the interface diffusion width of the pure tantalum plate layer and the pure aluminum interlayer is 1-5 mu m, the bonding strength is higher, and the use requirement is met.
The first aspect of the embodiment of the invention provides a light high-strength Mg-Al-Ta composite metal plate which is characterized by comprising a magnesium alloy plate layer, a pure aluminum intermediate layer, a pure tantalum plate layer, a pure aluminum intermediate layer and a magnesium alloy plate layer which are sequentially compounded and have diffusion interfaces between adjacent plate layers; the interface diffusion width of the pure tantalum plate layer and the pure aluminum intermediate layer is 1-5 mu m.
In one possible implementation, the thickness of the pure aluminum interlayer is 0.01-0.15mm; the thickness of the magnesium alloy plate layer is 0.1-3.0 mm; the thickness of the pure tantalum plate layer is 0.1-3 mm.
The second aspect of the embodiment of the invention provides a roll forming method of a light high-strength Mg-Al-Ta composite metal plate, which is characterized by comprising the following steps of:
(1) Taking a selected magnesium alloy plate for pre-annealing treatment; sequentially and selectively carrying out surface treatment and heat preservation treatment on the selected pure tantalum plate, pure aluminum plate and the magnesium alloy plate subjected to pre-annealing treatment;
(2) Sequentially stacking the magnesium alloy plate, the pure aluminum plate and the pure tantalum plate according to the structure of the composite metal plate, and performing warm rolling forming to obtain the composite plate;
(3) And annealing the rolled composite plate.
In one possible implementation manner, in the step (1), the thickness ratio of the pure tantalum plate to the magnesium alloy plate is 1:1-10; the thickness ratio of the pure tantalum plate to the pure aluminum plate is 1:0.01-0.1; meanwhile, the thickness of the magnesium alloy plate is 0.2-6 mm when the thickness of the pure tantalum plate is 0.2-3 mm, and the thickness of the pure aluminum plate is 0.01-0.3 mm.
In one possible implementation, in the surface treatment, the roughness (Ra) after the surface treatment of the pure tantalum plate, the pure aluminum plate, and the magnesium alloy plate is controlled to be in the range of 100-500 μm.
In one possible implementation, in the heat preservation treatment, the pure tantalum plate is kept at 150-550 ℃ for 10-40min, and the magnesium alloy plate is kept at 100-300 ℃ for 10-30min.
In one possible implementation manner, in the step (1), the annealing heat treatment process of the magnesium alloy sheet is as follows: preserving the temperature at 150-250 ℃ for 1-5h, and air-cooling to room temperature.
In one possible implementation manner, in the step (2), warm rolling forming control parameters are as follows: the temperature of the roller is 150-250 ℃, the rolling pass is performed at least once, and the reduction of the first pass is 40-70%.
In one possible implementation manner, in the step (3), the annealing process control parameters are: the annealing temperature is 100-300 ℃, the heat preservation time is 1-3h, and the cooling mode is cooling along with the furnace or air cooling outside the furnace.
The invention also discloses an application of the light high-strength Mg-Al-Ta composite metal plate or the light high-strength Mg-Al-Ta composite metal plate formed by the method in the aerospace field.
According to the light high-strength Mg-Al-Ta composite metal plate, the interface diffusion between magnesium and aluminum and between tantalum and aluminum is promoted by adding the rolled pure aluminum intermediate layer, so that the magnesium metal and the tantalum metal are connected through the intermediate layer. Because the light metal such as metal aluminum has lower density, and the extensibility is good, the light metal is suitable for being combined with other metals. The research of the scheme of the invention shows that the magnesium-aluminum binary phase diagram shown in figure 2 can realize element diffusion between magnesium and aluminum from 0 ℃, and a solid solution can be completely formed between two metal components with any component ratio at about 450 ℃, so that the bonding performance between the two materials is excellent. The binary phase diagram of aluminum-tantalum as shown in fig. 3 shows that aluminum and tantalum diffuse more easily into tantalum as the aluminum content is reduced, and tantalum components can be completely dissolved in the aluminum at about 300 ℃ at the lowest when the aluminum content is extremely low, and compounds between aluminum and tantalum appear in the binary phase diagram when the aluminum content is increased, and solid solution structures between aluminum and tantalum can be generated at lower temperature.
According to the forming method of the light high-strength Mg-Al-Ta composite metal plate, in order to promote the smooth performance of interface metallurgical bonding and rolling between magnesium alloy and pure tantalum, heat preservation treatment and warm rolling forming are adopted, so that the diffusion speed of interface atoms can be increased, the diffusion and fusion of the interface atoms are effectively promoted, further, effective metallurgical bonding is rapidly formed, a mechanical and metallurgical coexisting high-strength interface is formed, but the rolling temperature is controlled, and the phenomenon that the bonding strength of the composite metal plate is influenced by too wide interface diffusion width or more alloy phases with lower strength formed by the interface is prevented. In conclusion, the aluminum layer metal is adopted as a rolling combination medium of magnesium and tantalum, and the magnesium alloy and other metals of the dissimilar metal are rolled and formed through a warm rolling process. And meanwhile, support is provided for the development of a special shielding structure of the deep space exploration spacecraft.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings that are needed in the embodiments will be briefly described below, it being understood that the following drawings only illustrate some embodiments of the present invention and therefore should not be considered as limiting the scope, and other related drawings may be obtained according to these drawings without inventive effort for a person skilled in the art.
FIG. 1 is a binary phase diagram of Mg-Ta;
FIG. 2 is a binary phase diagram of Mg-Al;
FIG. 3 is a binary phase diagram of Al-Ta;
FIG. 4 is a flow chart of the warm rolling forming process of the magnesium-aluminum-tantalum composite board;
FIG. 5 is a scanning electron micrograph of a 40% (first pass) reduction rolled plate interface; wherein, (a) is AZ31B magnesium alloy plate which is not pre-annealed (comparative example 1), and Ta-Al-AZ31B is arranged on the left, middle and right in sequence; (b) Pre-annealing the AZ31B alloy plate (example 1), wherein Ta-Al-AZ31B is arranged on the left, middle and right in sequence;
FIG. 6 is a graph of the magnesium-aluminum interfacial diffusion width of a 40% (first pass) reduction composite panel; wherein, (a) is a magnesium-aluminum interface diffusion width graph (example 1) of the composite board after the pre-annealing treatment; (b) A magnesium-aluminum interface diffusion width graph (comparative example 1) of a composite board without pre-annealing treatment; (c) A tantalum-aluminum interface diffusion width graph (example 1) of the composite plate after pre-annealing treatment;
FIG. 7 is a graph of the stress-strain curve of the rolling engineering of the composite sheet material of the present invention in each pass;
FIG. 8 is a morphology of a magnesium/tantalum composite metal sheet after a first pass rolling;
FIG. 9 is a morphology of a magnesium/tantalum composite metal sheet after a second pass rolling;
fig. 10 is a morphology of the magnesium/tantalum composite metal plate after the third pass of rolling.
Detailed Description
For the purpose of making the objects, technical solutions and advantages of the embodiments of the present invention more apparent, the technical solutions of the embodiments of the present invention will be clearly and completely described below with reference to the accompanying drawings in the embodiments of the present invention, and it is apparent that the described embodiments are some embodiments of the present invention, but not all embodiments of the present invention. The components of the embodiments of the present invention generally described and illustrated in the figures herein may be arranged and designed in a wide variety of different configurations.
Thus, the following detailed description of the embodiments of the invention, as presented in the figures, is not intended to limit the scope of the invention, as claimed, but is merely representative of selected embodiments of the invention. All other embodiments, which can be made by those skilled in the art based on the embodiments of the invention without making any inventive effort, are intended to be within the scope of the invention.
It should be noted that: like reference numerals and letters denote like items in the following figures, and thus once an item is defined in one figure, no further definition or explanation thereof is necessary in the following figures.
In the following embodiments of the present invention, the preparation materials of the light high-strength Mg-Al-Ta composite metal sheet include AZ31B magnesium alloy sheet, 1060 aluminum sheet (pure aluminum sheet) and experimental high-purity tantalum sheet, wherein the pure tantalum sheet has the following composition ranges: c-0.01%, H-0.015%, O-0.015%, nb-0.05%, fe-0.005%, W-0.01%, mo-0.01%, si-0.005% and the balance Ta. The chemical components of the AZ31B magnesium alloy plate and the 1060 aluminum plate meet the specifications in the national standards GB/T5153-2016 and GB/T3190-2020. The thickness ratio of the pure tantalum plate to the magnesium alloy plate is 1:1-10; the thickness ratio of the pure tantalum plate to the 1060 aluminum plate is 1:0.01-0.1; meanwhile, when the thickness of the pure tantalum plate is 0.2-3 mm, the thickness of the magnesium alloy plate is 0.2-6 mm, and the thickness of the 1060 aluminum plate is 0.01-0.3 mm.
Example 1
As shown in fig. 4, the roll forming method of the light high-strength Mg-Al-Ta composite metal plate according to the embodiment includes the following steps: (1) AZ31B magnesium alloy plates were prepared, 1060 aluminum plates (i.e., pure aluminum plates) and pure tantalum plates, the AZ31B magnesium alloy plates had a thickness of 2.+ -. 0.1mm, the 1060 aluminum plates had a thickness of 0.1.+ -. 0.02mm, and the pure tantalum plates had a thickness of 2.+ -. 0.1mm. The dimensions of the specific materials are shown in table 1 below;
TABLE 1 magnesium/aluminum/tantalum sheet size diagram
Firstly, carrying out pretreatment, namely respectively carrying out surface pretreatment on a pure tantalum plate and an AZ31B magnesium alloy plate by using a sand mill, wherein the surface pretreatment comprises the steps of removing surface defects, impurities and an oxide layer, wherein the thickness of the oxide layer is not less than 1 mu m, determining the thickness of the oxide layer to be removed based on the specific condition of the surface of the plate to thoroughly remove stains on the surface of the plate, and then carrying out pre-annealing treatment on the AZ31B magnesium alloy plate to eliminate the internal stress of the AZ31B magnesium alloy plate, wherein the temperature of 150-250 ℃ can be selected, the heat preservation time is 1-5h, and the AZ31B magnesium alloy plate is treated by adopting an annealing process with the pre-annealing temperature of 150 ℃ for 1h, so that if the preparation requirement of the composite metal plate is met, other processes higher than the temperature can also meet the preparation requirement of the composite metal plate; then carrying out secondary surface treatment on the pure tantalum plate, the 1060 aluminum plate and the AZ31B magnesium alloy plate, wherein the surface roughness Ra of the treated pure tantalum plate, the 1060 aluminum plate and the AZ31B magnesium alloy plate is about 100 mu m, and the adopted surface treatment process is not limited to a steel brush, a sand mill, an angle mill, sand paper, laser polishing or electrochemical etching and other modes; since the lower the surface roughness of the sheet material is, the smaller the mechanical bonding strength is when the sheet material is compounded, the experiment is performed by selecting the surface roughness of 100 μm, and the mechanical bonding strength is higher when the parameter of the roughness of more than 100 μm is adopted. The method comprises the steps of carrying out surface cleaning treatment on a polished AZ31B magnesium alloy plate, a 1060 aluminum plate and a pure tantalum plate, wherein the cleaning step is to wipe the polished material surface with absolute ethyl alcohol to remove greasy dirt left by polishing and the like, concretely, a cotton ball is adopted to dip absolute ethyl alcohol to uniformly wipe the material surface, then the pure tantalum plate and the pre-annealed AZ31B magnesium alloy plate are subjected to heat preservation treatment before rolling, the pure tantalum plate is subjected to heat preservation at 150-550 ℃ for 10-40min, and the magnesium alloy plate is subjected to heat preservation at 100-300 ℃ for 10-30min. In general, the lower the holding temperature, the lower the metallurgical bonding strength in the warm rolling process, so the higher the holding temperature is generally, but at the same time, it should be noted that pure tantalum plates are easily oxidized at high temperature, and a proper temperature interval can improve the metallurgical bonding strength of plate compounding on one hand and reduce the formation of oxides of the plates in the warm rolling bonding on the other hand. The pure tantalum plate of the embodiment is kept at the temperature of 150+/-5 ℃ for 10min, and the AZ31B magnesium alloy plate is kept at the temperature of 100+/-5 ℃ for 10min.
Because the 1060 aluminum plate is thinner, heat preservation is not needed, the pure tantalum plate has good processability and high elongation although the melting point is high, and the heat preservation is only needed for at least 10 minutes without annealing treatment; in addition, in order to facilitate the preparation of the aluminum plates, the thicknesses of the two 1060 aluminum plates in the rolling process are set to be the same; however, the 1060 aluminum plate in the present invention may have different thickness specifications.
(2) The AZ31B-Al-Ta-Al-AZ31B are sequentially stacked and rolled, the roller temperature is 150 ℃, the roller speed is 0.1-0.3m/s, the speed difference between 0.1m/s and 0.3m/s is not great, and the influence on the forming performance of the plate is small; the first pass rolling reduction is between 40 and 70 percent, the first pass rolling reduction is too small, and the plates are difficult to combine, so that the metal plates fail to be compounded and cannot be rolled in the next step; the rolling reduction is too large, so that the rolling is easy to crack; in this example, the first pass reduction was 40%.
(3) Annealing the rolled Mg-Al-Ta composite metal plate, wherein the annealing temperature is 100-300 ℃, the heat preservation time is 1-3h, and the reason for selecting the interval is as follows: when the annealing temperature is low, the effect of removing the internal stress of the composite metal plate is poor; the solid solution between the plates is melted at first due to the fact that the temperature is too high, the interface bonding strength is reduced, the stress in the pure tantalum plate and the AZ31B magnesium alloy plate is large, the pure tantalum plate and the AZ31B magnesium alloy plate deform under the action of the stress in the pure tantalum plate and the AZ31B magnesium alloy plate, and the Mg-Al-Ta composite metal plate is prone to cracking from the interface. In this example, it is preferable to keep the temperature at 150℃for 1 hour, and cool or air-cool the temperature in the furnace.
Comparative example 1
The method for preparing the light high-strength Mg-Al-Ta composite metal sheet according to this comparative example is the same as that of example 1, except that in the step (1), the AZ31B magnesium alloy sheet is not subjected to the pre-annealing treatment.
Comparative example 2
The roll forming method of the light high-strength Mg-Al-Ta composite metal sheet according to the present comparative example is the same as that of example 1, and is characterized in that in the step (1), the pure tantalum sheet and the pre-annealed AZ31B magnesium alloy sheet are not subjected to heat preservation treatment before rolling; in the step (2), the roll temperature is normal. At this time, the mg—al—ta composite metal plate was not rolled successfully.
As shown in fig. 5, when the first pass reduction is 40%, the interface scanning electron micrograph of the rolled plate of example 1 and comparative example 1 shows that the Mg-Al-Ta interface is tightly bonded and mechanically connected in both processes.
As shown in fig. 6, when the first pass reduction is 40%, the Mg-Al diffusion interface of the rolled sheet material of example 1 and comparative example 1 and the Al-Ta diffusion interface of the rolled sheet material of example 1 are scanned in a line, the line scanning curve areas of example 1 and comparative example 1 are smooth at the Mg-Al interface, the Mg-Al composite plate is subjected to partial element diffusion, but no obvious intermediate diffusion layer is formed, the line scanning result shows that the diffusion layer width is increased after the AZ31B magnesium alloy sheet is subjected to the pre-annealing treatment, which indicates that the bonding at the Mg-Al interface is enhanced, and the diffusion widths of the AZ31B magnesium alloy sheet subjected to the pre-annealing treatment and the AZ31B magnesium alloy sheet not subjected to the pre-annealing treatment are respectively 4.8 μm and 4.2 μm at the Mg-Al interface. Therefore, the AZ31B magnesium alloy plate subjected to the pre-annealing treatment can increase the diffusion width at the magnesium-aluminum interface to a certain extent, so that the metallurgical bonding of the rolled plate interface is increased to a certain extent.
At the Al-Ta interface, as shown in FIG. 6c, the line scan curve area of example 1 was smooth, and the Al-Ta composite plate had some elemental diffusion but no significant intermediate diffusion layer formation, and the Al-Ta interface diffusion widths were measured to be 1.4 μm, respectively. Therefore, the diffusion width of the Al-Ta interface can be increased to a certain extent by warm rolling to form the composite metal plate, so that the metallurgical bonding strength of the interface of the pricked plate is increased to a certain extent.
And (3) on the basis of successful combination of the first pass rolling, the annealing treatment in the step (3) is not performed, and the second pass rolling is continuously performed on the composite metal sheet, wherein the parameters are the same as those of the scheme of the embodiment 1, and the difference is that the rolling reduction is controlled to be 20%, so that the Mg-Al-Ta composite metal sheet after the second pass rolling is obtained.
On the basis of the Mg-Al-Ta composite metal sheet after the second pass rolling, the second pass rolling is continuously carried out on the composite metal sheet, and the parameters are the same as those of the scheme of the embodiment 1, wherein the difference is only that the rolling reduction is controlled to be 20 percent, so that the magnesium/tantalum composite metal sheet after the third pass rolling is obtained.
As shown in fig. 7, the tensile strength of the Mg-Al-Ta composite metal sheet is gradually increased with increasing rolling passes, and the tensile strength of the composite sheet is (162±50) MPa, (274±10) MPa, and (342±15) MPa under 1, 2, and 3 passes of rolling, respectively, according to the true stress-strain curves of the Mg-Al-Ta composite metal sheet in the first pass, the second pass, and the third pass.
After the Mg-Al-Ta composite metal plate passes through the first pass, the second pass and the third pass, the diffusion widths of the Mg-Al interface are sequentially 4.8, 5.0 and 5.1 mu m, and the diffusion widths of the Al-Ta interface are sequentially 1.4, 1.4 and 1.9 mu m; the rolled shape is shown in fig. 8-10.
Example 2
The roll forming method of the light high-strength Mg-Al-Ta composite metal plate comprises the following steps of: (1) Preparing AZ31B magnesium alloy, 1060 aluminum plate and pure tantalum plate, wherein the performances and the sizes of the plates are the same as those of the example 1; respectively carrying out surface pretreatment on a pure tantalum plate and an AZ31B magnesium alloy plate by using a sand mill, removing an oxide layer with the thickness not smaller than 1 mu m, and then carrying out pre-annealing heat treatment on the AZ31B magnesium alloy plate at the temperature of 180 ℃ for 3 hours; and then carrying out secondary surface treatment on the pure tantalum plate, the 1060 aluminum plate and the AZ31B magnesium alloy plate, wherein the surface roughness Ra of the treated plate is about 200 mu m, cleaning the surface of the plate by absolute ethyl alcohol, then carrying out heat preservation treatment before rolling on the pure tantalum plate and the annealed AZ31B magnesium alloy plate, wherein the pure tantalum plate is kept at 200+/-5 ℃ for 30min, and the AZ31B magnesium alloy plate is kept at 150+/-5 ℃ for 30min.
(2) The roller temperature is 170 ℃, the roller speed is 0.1-0.3m/s, and the first pass reduction is 50%.
(3) Annealing the rolled composite board under protective atmosphere, wherein the specific annealing parameters are as follows: preserving heat for 2h at 200 ℃, and cooling along with the furnace.
The light high-strength Mg-Al-Ta composite metal plate is obtained, and the diffusion width of an aluminum-tantalum interface is 2.1 mu m.
Example 3
The roll forming method of the light high-strength Mg-Al-Ta composite metal plate comprises the following steps of: (1) Preparing AZ31B magnesium alloy, 1060 aluminum plate and pure tantalum plate, wherein the performances and the sizes of the plates are the same as those of the example 1; respectively carrying out surface pretreatment on a pure tantalum plate and an AZ31B magnesium alloy plate by using a sand mill, removing an oxide layer with the thickness not smaller than 1 mu m, and then carrying out annealing heat treatment on the AZ31B magnesium alloy plate at 220 ℃ for 4 hours; and then carrying out secondary surface treatment on the pure tantalum plate, the 1060 aluminum plate and the AZ31B magnesium alloy plate, wherein the surface roughness Ra of the treated plate is about 300 mu m, cleaning the surface of the plate by absolute ethyl alcohol, then carrying out heat preservation treatment before rolling on the pure tantalum plate and the heat treated AZ31B magnesium alloy plate, wherein the pure tantalum plate is kept at 400+/-5 ℃ for 30min, and the AZ31B magnesium alloy plate is kept at 260+/-5 ℃ for 30min.
(2) The roller temperature is 220 ℃, the roller speed is 0.1-0.3m/s, and the first pass reduction is 65%.
(3) Annealing the rolled composite board under protective atmosphere, wherein the specific annealing parameters are as follows: preserving heat for 2h at 260 ℃, and cooling along with the furnace.
The light high-strength Mg-Al-Ta composite metal plate is obtained, and the diffusion width of an aluminum-tantalum interface is 4.5 mu m.
Example 4
The roll forming method of the light high-strength Mg-Al-Ta composite metal plate comprises the following steps of: (1) AZ31B magnesium alloy plates were prepared, 1060 aluminum plates (i.e., pure aluminum plates) and pure tantalum plates, the AZ31B magnesium alloy plates had a thickness of 2.+ -. 0.1mm, the 1060 aluminum plates had a thickness of 0.05.+ -. 0.001mm, and the pure tantalum plates had a thickness of 2.+ -. 0.1mm. The dimensions of the specific materials are shown in table 2 below;
TABLE 2 magnesium/aluminum/tantalum sheet size diagram
Respectively carrying out surface pretreatment on a pure tantalum plate and an AZ31B magnesium alloy plate by using a sand mill, removing an oxide layer with the thickness not smaller than 1 mu m, and then carrying out annealing heat treatment on the AZ31B magnesium alloy plate at the temperature of 200 ℃ for 3 hours; and then carrying out secondary surface treatment on the pure tantalum plate, the 1060 aluminum plate and the AZ31B magnesium alloy plate, wherein the surface roughness Ra of the treated plate is about 250 mu m, cleaning the surface of the plate by absolute ethyl alcohol, then carrying out heat preservation treatment before rolling on the pure tantalum plate and the heat treated AZ31B magnesium alloy plate, wherein the pure tantalum plate is kept at 400+/-5 ℃ for 30min, and the AZ31B magnesium alloy plate is kept at 200+/-5 ℃ for 30min.
Because the aluminum plate is thinner, heat preservation treatment is not needed, and in addition, the pure tantalum plate has high melting point, but good processability and high elongation, and annealing treatment is not needed.
(2) The rolling is carried out according to AZ31B-Al-Ta-Al-AZ31B, the roller temperature is 170 ℃, the roller speed is 0.1-0.3m/s, the initial pass rolling reduction is about 45%, and the 2-3 pass rolling reduction is 20% and 30% respectively.
(3) Annealing the rolled Mg-Al-Ta composite metal plate in a protective atmosphere, wherein the specific annealing parameters are as follows: preserving heat for 2h at 200 ℃, and cooling along with the furnace.
The light high-strength Mg-Al-Ta composite metal plate is obtained, and the diffusion width of an aluminum-tantalum interface is 4.6 mu m.
Example 5
The roll forming method of the light high-strength Mg-Al-Ta composite metal plate comprises the following steps of: (1) AZ31B magnesium alloy plates were prepared, 1060 aluminum plates (i.e., pure aluminum plates) and pure tantalum plates, the AZ31B magnesium alloy plates had a thickness of 2.+ -. 0.1mm, the 1060 aluminum plates had a thickness of 0.01.+ -. 0.001mm, and the pure tantalum plates had a thickness of 2.+ -. 0.1mm. The dimensions of the specific materials are shown in table 3 below;
TABLE 3 magnesium/aluminum/tantalum sheet size diagram
Respectively carrying out surface pretreatment on a pure tantalum plate and an AZ31B magnesium alloy plate by using a sand mill, removing an oxide layer with the thickness not smaller than 1 mu m, and then carrying out annealing heat treatment on the AZ31B magnesium alloy plate at the temperature of 200 ℃ for 3 hours; and then carrying out secondary surface treatment on the pure tantalum plate, the 1060 aluminum plate and the AZ31B magnesium alloy plate, wherein the surface roughness Ra of the treated plate is about 100 mu m, cleaning the surface of the plate by absolute ethyl alcohol, then carrying out heat preservation treatment before rolling on the pure tantalum plate and the heat treated AZ31B magnesium alloy plate, wherein the pure tantalum plate is kept at the temperature of 450+/-5 ℃ for 30min, and the AZ31B magnesium alloy plate is kept at the temperature of 225+/-5 ℃ for 30min.
Because the aluminum plate is thinner, heat preservation treatment is not needed, and in addition, the pure tantalum plate has high melting point, but good processability and high elongation, and annealing treatment is not needed.
(2) The rolling is carried out by stacking AZ31B-Al-Ta-Al-AZ31B in sequence, the roller temperature is 170 ℃, the roller speed is 0.15m/s, the initial pass reduction is about 40%, and the 2-3 pass reduction is 20% and 30% respectively.
(3) Annealing the rolled Mg-Al-Ta composite metal plate in a protective atmosphere, wherein the specific annealing parameters are as follows: preserving heat for 2h at 250 ℃, and cooling along with the furnace.
The light high-strength Mg-Al-Ta composite metal plate is obtained, and the diffusion width of an aluminum-tantalum interface is 4.6 mu m.
Example 6
The roll forming method of the light high-strength Mg-Al-Ta composite metal plate comprises the following steps of: (1) Preparing AZ31B magnesium alloy, 1060 aluminum plate and pure tantalum plate, wherein the performances and the sizes of the plates are the same as those of the example 5; respectively carrying out surface pretreatment on a pure tantalum plate and an AZ31B magnesium alloy plate by using a sand mill, removing an oxide layer with the thickness not smaller than 1 mu m, and then carrying out annealing heat treatment on the AZ31B magnesium alloy plate at the temperature of 200 ℃ for 3 hours; and then carrying out secondary surface treatment on the pure tantalum plate, the 1060 aluminum plate and the AZ31B magnesium alloy plate, wherein the surface roughness Ra of the treated plate is about 100 mu m, cleaning the surface of the plate by absolute ethyl alcohol, then carrying out heat preservation treatment before rolling on the pure tantalum plate and the heat treated AZ31B magnesium alloy plate, wherein the pure tantalum plate is kept at the temperature of 450+/-5 ℃ for 30min, and the AZ31B magnesium alloy plate is kept at the temperature of 225+/-5 ℃ for 30min.
(2) The rolling is carried out by stacking AZ31B-Al-Ta-Al-AZ31B in sequence, the roller temperature is 170 ℃, the roller speed is 0.1-0.3m/s, the initial pass reduction is about 40%, and the 2-3 pass reduction is 20% and 30% respectively.
(3) Annealing the rolled Mg-Al-Ta composite metal plate in a protective atmosphere, wherein the specific annealing parameters are as follows: preserving heat for 2h at 250 ℃, and cooling along with the furnace.
The light high-strength Mg-Al-Ta composite metal plate is obtained, and the diffusion width of an aluminum-tantalum interface is 4.7 mu m.
The above is only a preferred embodiment of the present invention, and is not intended to limit the present invention, but various modifications and variations can be made to the present invention by those skilled in the art. Any modification, equivalent replacement, improvement, etc. made within the spirit and principle of the present invention should be included in the protection scope of the present invention.
Claims (10)
1. A light high-strength Mg-Al-Ta composite metal plate is characterized in that,
the composite material comprises a magnesium alloy plate layer, a pure aluminum intermediate layer, a pure tantalum plate layer, a pure aluminum intermediate layer and a magnesium alloy plate layer which are sequentially compounded and diffusion interfaces exist between adjacent plate layers; the interface diffusion width of the pure tantalum plate layer and the pure aluminum intermediate layer is 1-5 mu m, and a solid solution structure is formed between the pure tantalum plate layer and the pure aluminum intermediate layer.
2. The light high-strength Mg-Al-Ta composite sheet metal of claim 1, said pure aluminum interlayer having a thickness of 0.01-0.15mm; the thickness of the magnesium alloy plate layer is 0.1-3.0 mm; the thickness of the pure tantalum plate layer is 0.1-3 mm.
3. The roll forming method of a light high-strength Mg-Al-Ta composite metal sheet according to claim 1 or 2, comprising the steps of,
the method comprises the following steps:
(1) Taking a selected magnesium alloy plate for pre-annealing treatment; sequentially and selectively carrying out surface treatment and heat preservation treatment on the selected pure tantalum plate, pure aluminum plate and the magnesium alloy plate subjected to pre-annealing treatment;
(2) Sequentially stacking the magnesium alloy plate, the pure aluminum plate and the pure tantalum plate according to the structure of the composite metal plate, and performing warm rolling forming to obtain the composite plate;
(3) And annealing the rolled composite plate.
4. The roll forming method of a light high-strength Mg-Al-Ta composite metal sheet according to claim 3, comprising the steps of,
in the step (1), the thickness ratio of the pure tantalum plate to the magnesium alloy plate is 1:1-10; the thickness ratio of the pure tantalum plate to the pure aluminum plate is 1:0.01-0.1; meanwhile, the thickness of the magnesium alloy plate is 0.2-6 mm when the thickness of the pure tantalum plate is 0.2-3 mm, and the thickness of the pure aluminum plate is 0.01-0.3 mm.
5. The roll forming method of a light high-strength Mg-Al-Ta composite metal sheet according to claim 3, comprising the steps of,
in the surface treatment, the roughness (Ra) of the pure tantalum plate, the pure aluminum plate and the magnesium alloy plate after the surface treatment is controlled to be in the range of 100-500 mu m.
6. The roll forming method of a light high-strength Mg-Al-Ta composite metal sheet according to claim 3, comprising the steps of,
in the heat preservation treatment, the pure tantalum plate is subjected to heat preservation at 150-550 ℃ for 10-40min, and the magnesium alloy plate is subjected to heat preservation at 100-300 ℃ for 10-30min.
7. The roll forming method of a light high-strength Mg-Al-Ta composite metal sheet according to claim 3, comprising the steps of,
in the step (1), the annealing heat treatment process of the magnesium alloy plate comprises the following steps: preserving the temperature at 150-250 ℃ for 1-5h, and air-cooling to room temperature.
8. The roll forming method of a light high-strength Mg-Al-Ta composite metal sheet according to claim 3, comprising the steps of,
in the step (2), warm rolling forming control parameters are as follows: the temperature of the roller is 150-250 ℃, the rolling pass is performed at least once, and the reduction of the first pass is 40-70%.
9. The roll forming method of a light high-strength Mg-Al-Ta composite metal sheet according to claim 3, comprising the steps of,
in the step (3), the annealing treatment control parameters are as follows: the annealing temperature is 100-300 ℃, the heat preservation time is 1-3h, and the cooling mode is cooling along with the furnace or air cooling outside the furnace.
10. Use of the light high-strength Mg-Al-Ta composite metal sheet according to claim 1 or 2 or the light high-strength Mg-Al-Ta composite metal sheet obtained by molding according to any one of claims 3 to 9 in the aerospace field.
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