CN116555629A - High-strength high-damping Al-Zn eutectoid damping alloy and preparation method thereof - Google Patents
High-strength high-damping Al-Zn eutectoid damping alloy and preparation method thereof Download PDFInfo
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 110
- 239000000956 alloy Substances 0.000 title claims abstract description 110
- 238000013016 damping Methods 0.000 title claims abstract description 100
- 229910018137 Al-Zn Inorganic materials 0.000 title claims abstract description 54
- 229910018573 Al—Zn Inorganic materials 0.000 title claims abstract description 54
- 238000002360 preparation method Methods 0.000 title claims abstract description 13
- 238000000265 homogenisation Methods 0.000 claims abstract description 15
- 238000001192 hot extrusion Methods 0.000 claims abstract description 12
- 238000000034 method Methods 0.000 claims abstract description 10
- 238000004519 manufacturing process Methods 0.000 claims abstract description 4
- 229910052782 aluminium Inorganic materials 0.000 claims description 32
- 238000010438 heat treatment Methods 0.000 claims description 29
- 239000011701 zinc Substances 0.000 claims description 29
- 229910000636 Ce alloy Inorganic materials 0.000 claims description 28
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 28
- 238000001816 cooling Methods 0.000 claims description 23
- 229910018575 Al—Ti Inorganic materials 0.000 claims description 22
- 238000007664 blowing Methods 0.000 claims description 18
- 239000002893 slag Substances 0.000 claims description 18
- 238000004321 preservation Methods 0.000 claims description 12
- 229910052725 zinc Inorganic materials 0.000 claims description 12
- 238000001125 extrusion Methods 0.000 claims description 10
- 238000005266 casting Methods 0.000 claims description 9
- 239000002994 raw material Substances 0.000 claims description 9
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 8
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 8
- 229910000838 Al alloy Inorganic materials 0.000 claims description 2
- 239000007788 liquid Substances 0.000 claims description 2
- 239000000203 mixture Substances 0.000 claims description 2
- 239000002054 inoculum Substances 0.000 abstract description 2
- 230000008569 process Effects 0.000 abstract description 2
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 24
- 229910052786 argon Inorganic materials 0.000 description 12
- 239000007789 gas Substances 0.000 description 8
- 230000000052 comparative effect Effects 0.000 description 7
- 238000010892 electric spark Methods 0.000 description 7
- 238000003825 pressing Methods 0.000 description 6
- 238000012545 processing Methods 0.000 description 5
- 230000006698 induction Effects 0.000 description 4
- 238000002844 melting Methods 0.000 description 4
- 230000008018 melting Effects 0.000 description 4
- 238000005096 rolling process Methods 0.000 description 4
- 238000005303 weighing Methods 0.000 description 4
- 238000003754 machining Methods 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- 238000005520 cutting process Methods 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 239000002086 nanomaterial Substances 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 238000011056 performance test Methods 0.000 description 2
- 230000005501 phase interface Effects 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 238000011160 research Methods 0.000 description 2
- 229920000426 Microplastic Polymers 0.000 description 1
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- 239000000463 material Substances 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
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- 230000000930 thermomechanical effect Effects 0.000 description 1
- 229920001169 thermoplastic Polymers 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C18/00—Alloys based on zinc
- C22C18/04—Alloys based on zinc with aluminium as the next major constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
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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
- C22F1/165—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 of zinc or cadmium or alloys based thereon
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
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Abstract
The invention discloses a high-strength high-damping Al-Zn eutectoid damping alloy and a preparation method thereof, wherein the alloy comprises the following components in percentage by atom: 45-54 at.% of Al, 45-54 at.% of Zn, 0.05-0.5 at.% of Ce and 0.5-2 at.% of Ti. The microstructure of the Al-Zn eutectoid damping alloy can be refined by adding trace Ti and Ce elements as inoculants and modificators, and the multiscale micro-nano-level alpha+eta eutectoid structure can be further obtained by adjusting the hot extrusion process of the alloy after homogenization treatment. The tensile strength of the Al-Zn eutectoid damping alloy prepared by the method can reach 390MPa, the mechanical property is obviously improved compared with the existing Al-Zn alloy, and the preparation method of the high-strength high-damping Al-Zn eutectoid damping alloy prepared by the method is simple, is easy to operate, has low production cost and has wide application prospect.
Description
Technical Field
The invention belongs to the technical field of damping alloy, and particularly relates to a high-strength high-damping Al-Zn eutectoid damping alloy and a preparation method thereof.
Background
With the development of modern industry, the control of vibration and noise reduction are increasingly receiving great attention from various industries. Vibration and noise not only can negatively affect the quality, service life, precision and raw material consumption of products, but also can not be ignored, and vibration and noise can be reduced or prevented from sources by adopting vibration reduction materials.
The Al-Zn eutectoid damping alloy is paid attention to because of high damping capacity and good processability, and has wide application prospect in the fields of aerospace, rail transit, automobiles and the like. The research shows that the Al-Zn eutectoid damping alloy belongs to a complex phase damping alloy, and the damping mechanism is mainly the viscous sliding of an alpha/eta phase interface and is assisted by the micro plastic deformation of an alpha phase. However, al-Zn eutectoid damping alloys have relatively poor mechanical properties, in particular relatively low tensile strength. According to the report of related literature, the tensile strength of Al-Zn base damping alloy is generally less than 300MPa, which limits the wider application of the alloy to a certain extent. Therefore, the comprehensive performance of the Al-Zn eutectoid damping alloy is improved, and the mechanical property of the Al-Zn eutectoid damping alloy has very important significance for research, development and application of the alloy.
Disclosure of Invention
Aiming at the prior art, the invention provides a high-strength high-damping Al-Zn eutectoid damping alloy and a preparation method thereof, so as to solve the technical problem of poor mechanical property of the Al-Zn eutectoid damping alloy.
In order to achieve the above purpose, the technical scheme adopted by the invention is as follows: provided is a high-strength high-damping Al-Zn eutectoid damping alloy, comprising, in atomic percent: 45-54 at.% of Al, 45-54 at.% of Zn, 0.05-0.5 at.% of Ce and 0.5-2 at.% of Ti.
On the basis of the technical scheme, the invention can be improved as follows.
Further, the high-strength high-damping Al-Zn eutectoid damping alloy comprises the following components in atom percent: al 50at.%, zn 48.9at.%, ce 0.1at.% and Ti 1at.%.
The invention also discloses a preparation method of the high-strength high-damping Al-Zn eutectoid damping alloy, which comprises the following steps:
s1: preparing raw materials according to an alloy composition ratio, wherein the raw materials comprise an aluminum block, a zinc block, an Al-Ce alloy block and an Al-Ti alloy block, the mass ratio of Ce in the Al-Ce alloy block is 10%, and the mass ratio of Ti in the Al-Ti alloy block is 10%;
s2: heating the aluminum block to 700-800 ℃ and preserving heat until the aluminum block is completely melted, then adding an Al-Ti alloy block into the aluminum liquid, blowing to remove slag after the aluminum block is completely melted, preserving heat for 15-25 min, then cooling to 630-670 ℃, adding a zinc block, blowing to remove slag after the aluminum block is completely melted, preserving heat for 15-25 min, then heating to 700-750 ℃ again, adding an Al-Ce alloy block into the zinc block, blowing to remove slag after the aluminum block is completely melted, and then cooling to room temperature along with a furnace to obtain a rough blank;
s3: heating the rough blank obtained in the step S2 to be molten, preserving heat for 15-25 min, and casting to obtain a primary ingot;
s4: homogenizing the initial ingot obtained in the step S3, and then cooling to room temperature by water;
s5: and (3) performing hot extrusion on the cast ingot subjected to the S4 treatment, and then performing water cooling to room temperature to obtain the aluminum alloy.
The preparation method can be further improved based on the technical scheme.
Further, the rate of the two heating in S2 is 3-6 ℃/min.
Further, the rate of two heats in S2 is 4 ℃/min.
Further, the final temperature of the aluminum block in S2 is 740 ℃, and the time of the first heat preservation is 20min; before zinc blocks are added, the system temperature is 660 ℃, and the second heat preservation time is 20min; the temperature of the system before adding the Al-Ce alloy block was 700 ℃.
Further, the homogenization treatment temperature in S4 is 350-400 ℃ and the treatment time is 18-22 h.
Further, the homogenization treatment temperature was 380℃and the treatment time was 20 hours.
Further, the hot extrusion temperature in S5 is 285-375 ℃, the extrusion rate is 0.1-10 mm/S, and the extrusion ratio is 6-16.
The beneficial effects of the invention are as follows:
1. the microstructure of the Al-Zn eutectoid damping alloy can be refined by adding trace Ti and Ce elements as inoculants and modificators, and the multiscale micro-nano-level alpha+eta eutectoid structure can be further obtained by adjusting the hot extrusion process of the alloy after homogenization treatment. Wherein the size of the eutectoid is about 4-6 μm, and the eutectoid presents micro-nano level structural characteristics with three scales: the first is an equiaxed granular structure, and the grain size is about 500-700 nm; the second is a lamellar structure with a certain length-diameter ratio (about 4:1), and the particle size is about 40-150 nm; the third is a nano-scale precipitation structure of eta-Zn in an alpha-Al matrix, and the size is about 10-20 nm. Namely, by adding trace Ti and Ce elements, the structure of the Al-Zn eutectoid damping alloy can be refined, and the area (the number of damping sources) of an alpha/eta phase interface is increased, so that the damping performance of the damping alloy is improved. In addition, the Al-Zn eutectoid damping alloy can further improve the damping performance and mechanical property of the alloy after further thermoplastic processing.
2. The tensile strength of the Al-Zn eutectoid damping alloy prepared in the invention can reach 390MPa, and the mechanical property is obviously improved compared with the existing Al-Zn alloy (the tensile strength of the Al-Zn base alloy reported in the literature is generally less than 300 MPa).
3. The multi-scale micro-nano Al-Zn eutectoid damping alloy prepared by the method has high strength and high damping performance.
4. The preparation method of the high-strength high-damping Al-Zn eutectoid damping alloy is simple, is easy to operate, has low production cost and has wide application prospect.
Drawings
FIG. 1 is an SEM photograph of a high-strength high-damping Al-Zn eutectoid damping alloy of example 1;
FIG. 2 is a TEM photograph of an equiaxed granular structure of the high-strength high-damping Al-Zn eutectoid damping alloy of example 1;
FIG. 3 is a TEM photograph of a layered structure of a high-strength high-damping Al-Zn eutectoid damping alloy sheet in an embodiment;
FIG. 4 is a TEM photograph of a high-strength high-damping Al-Zn eutectoid damping alloy nano-scale precipitation structure in an embodiment;
FIG. 5 is a room temperature elongation curve of the high-strength high-damping Al-Zn eutectoid damping alloy of example 1
FIG. 6 is a damping performance versus strain amplitude curve for the high-strength high-damping Al-Zn eutectoid damping alloy of example 1;
FIG. 7 is an SEM photograph of an Al-Zn eutectoid damping alloy of comparative example 1;
FIG. 8 is a room temperature tensile curve of the Al-Zn eutectoid damping alloy of comparative example 1;
FIG. 9 is a graph showing damping performance versus strain amplitude for the Al-Zn eutectoid damping alloy of comparative example 1.
Detailed Description
The following describes the present invention in detail with reference to examples.
Example 1
A high-strength high-damping Al-Zn eutectoid damping alloy comprising, in atomic percent, al 50at.%, zn 48.9at.%, ce 0.1at.% and Ti 1at.%.
The high-strength high-damping Al-Zn eutectoid damping alloy in the embodiment is prepared through the following steps:
s1: weighing an elemental Al block, an elemental Zn block, an Al-Ce alloy block and an Al-Ti alloy block according to the component proportion of 50at.% Al, 48.9at.% Zn, 0.1at.% Ce and 1at.% Ti, wherein the purity of each raw material is more than 99wt.%, the mass ratio of Ce in the Al-Ce alloy block is 10%, and the mass ratio of Ti in the Al-Ti alloy block is 10%;
s2: putting the aluminum block into a crucible of a well-type resistance furnace, heating the aluminum block to 740 ℃ at a heating rate of 4 ℃/min, and preserving heat until the aluminum block is completely melted; adding an Al-Ti alloy block, introducing argon gas for blowing after the Al-Ti alloy block is completely melted, removing slag, and preserving heat for 20min; then cooling to 660 ℃, adding Zn blocks, introducing argon gas for blowing after the Zn blocks are completely melted, removing slag, and preserving heat for 20min; heating to 700 ℃ again, adding an Al-Ce alloy block, pressing the Al-Ce alloy block into the bottom, introducing argon for blowing after all the Al-Ce alloy block is melted, removing slag, and preserving heat for 25min; cooling to room temperature along with the furnace after heat preservation is finished, and obtaining a rough blank;
s3: performing electric spark processing on the rough blank obtained in the step S2 to obtain a plurality of alloy blocks with smaller sizes, putting the alloy blocks into a vacuum induction melting furnace, gradually increasing the heating power to 15kW, preserving heat for 20min, and casting to obtain a primary ingot;
s4: placing the initial ingot obtained in the step S3 into a heat treatment furnace for homogenization treatment, wherein the homogenization treatment is to raise the temperature to 380 ℃ and keep the temperature for 20 hours, and taking out the initial ingot after the heat preservation is finished and cooling the initial ingot to room temperature;
s5: and (3) performing electric spark machining on the ingot casting subjected to homogenization treatment in the step (S4) to obtain a plurality of cylindrical samples with the diameter of 30mm and the height of 15mm, putting the cylindrical samples in a uniform state into a 200T four-column hydraulic press for hot extrusion, wherein the hot extrusion temperature is 375 ℃, the extrusion rate is 1mm/S, the extrusion ratio lambda is 9, and cooling to room temperature by water to obtain the high-strength high-damping Al-Zn eutectoid damping alloy.
Example 2
A high-strength high-damping Al-Zn eutectoid damping alloy comprising, in atomic percent, al 45at.%, zn 54at.%, ce 0.5at.% and Ti 0.5at.%.
The high-strength high-damping Al-Zn eutectoid damping alloy in the embodiment is prepared through the following steps:
s1: weighing an elemental Al block, an elemental Zn block, an Al-Ce alloy block and an Al-Ti alloy block according to the component proportion of 45at.% Al, 54at.% Zn, 0.5at.% Ce and 0.5at.% Ti, wherein the purity of each raw material is more than 99wt.%, the mass ratio of Ce in the Al-Ce alloy block is 10%, and the mass ratio of Ti in the Al-Ti alloy block is 10%;
s2: placing the aluminum block into a crucible of a well-type resistance furnace, heating the aluminum block to 700 ℃ at a heating rate of 3 ℃/min, and preserving heat until the aluminum block is completely melted; adding an Al-Ti alloy block, introducing argon gas for blowing after the Al-Ti alloy block is completely melted, removing slag, and preserving heat for 15min; then cooling to 630 ℃, adding Zn blocks, introducing argon gas for blowing after the Zn blocks are completely melted, removing slag, and preserving heat for 25min; heating to 700 ℃ again, adding an Al-Ce alloy block, pressing the Al-Ce alloy block into the bottom, introducing argon for blowing after all the Al-Ce alloy block is melted, removing slag, and preserving heat for 25min; cooling to room temperature along with the furnace after heat preservation is finished, and obtaining a rough blank;
s3: performing electric spark processing on the rough blank obtained in the step S2 to obtain a plurality of alloy blocks with smaller sizes, putting the alloy blocks into a vacuum induction melting furnace, gradually increasing the heating power to 15kW, preserving heat for 15min, and casting to obtain a primary ingot;
s4: placing the initial ingot obtained in the step S3 into a heat treatment furnace for homogenization treatment, wherein the homogenization treatment is to raise the temperature to 350 ℃ and keep the temperature for 22 hours, and taking out the initial ingot after the heat preservation is finished and cooling the initial ingot to room temperature;
s5: and (3) performing electric spark machining on the ingot casting subjected to homogenization treatment in the step (S4) to obtain a plurality of cylindrical samples with the diameter of 30mm and the height of 15mm, putting the cylindrical samples in a uniform state into a 200T four-column hydraulic press for hot extrusion, wherein the hot extrusion temperature is 285 ℃, the extrusion rate is 0.1mm/S, the extrusion ratio lambda is 6, and cooling to room temperature by water to obtain the high-strength high-damping Al-Zn eutectoid damping alloy.
Example 3
A high-strength high-damping Al-Zn eutectoid damping alloy comprising, in atomic percent, al 54at.%, zn 45at.%, ce 0.05at.% and Ti 0.95at.%.
The high-strength high-damping Al-Zn eutectoid damping alloy in the embodiment is prepared through the following steps:
s1: weighing an elemental Al block, an elemental Zn block, an Al-Ce alloy block and an Al-Ti alloy block according to the component proportion of 54at.% Al, 45at.% Zn, 0.05at.% Ce and 0.95at.% Ti, wherein the purity of each raw material is more than 99wt.%, the mass ratio of Ce in the Al-Ce alloy block is 10%, and the mass ratio of Ti in the Al-Ti alloy block is 10%;
s2: placing the aluminum block into a crucible of a well-type resistance furnace, heating the aluminum block to 800 ℃ at a heating rate of 3 ℃/min, and preserving heat until the aluminum block is completely melted; adding an Al-Ti alloy block, introducing argon gas for blowing after the Al-Ti alloy block is completely melted, removing slag, and preserving heat for 25min; then cooling to 670 ℃, adding Zn blocks, introducing argon gas for blowing after the Zn blocks are completely melted, removing slag, and preserving heat for 15min; heating to 750 ℃ again, adding an Al-Ce alloy block, pressing the Al-Ce alloy block into the bottom, introducing argon for blowing after all the Al-Ce alloy block is melted, removing slag, and preserving heat for 25min; cooling to room temperature along with the furnace after heat preservation is finished, and obtaining a rough blank;
s3: performing electric spark processing on the rough blank obtained in the step S2 to obtain a plurality of alloy blocks with smaller sizes, putting the alloy blocks into a vacuum induction melting furnace, gradually increasing the heating power to 15kW, preserving heat for 25min, and casting to obtain a primary ingot;
s4: placing the initial ingot obtained in the step S3 into a heat treatment furnace for homogenization treatment, wherein the homogenization treatment is to raise the temperature to 400 ℃ and keep the temperature for 18 hours, and taking out the initial ingot after the heat preservation is finished and cooling the initial ingot to room temperature;
s5: and (3) performing electric spark machining on the ingot casting subjected to homogenization treatment in the step (S4) to obtain a plurality of cylindrical samples with the diameter of 30mm and the height of 15mm, putting the cylindrical samples in a uniform state into a 200T four-column hydraulic press for hot extrusion, wherein the hot extrusion temperature is 375 ℃, the extrusion rate is 10mm/S, the extrusion ratio lambda is 16, and cooling to room temperature by water to obtain the high-strength high-damping Al-Zn eutectoid damping alloy.
Comparative example 1
A high-strength high-damping Al-Zn eutectoid damping alloy comprising, in atomic percent, al 50at.%, zn 48.9at.%, ce 0.1at.% and Ti 1at.%.
The high-strength high-damping Al-Zn eutectoid damping alloy in the embodiment is prepared through the following steps:
s1: weighing an elemental Al block, an elemental Zn block, an Al-Ce alloy block and an Al-Ti alloy block according to the component proportion of 50at.% Al, 48.9at.% Zn, 0.1at.% Ce and 1at.% Ti, wherein the purity of each raw material is more than 99wt.%, the mass ratio of Ce in the Al-Ce alloy block is 10%, and the mass ratio of Ti in the Al-Ti alloy block is 10%;
s2: putting the aluminum block into a crucible of a well-type resistance furnace, heating the aluminum block to 740 ℃ at a heating rate of 4 ℃/min, and preserving heat until the aluminum block is completely melted; adding an Al-Ti alloy block, introducing argon gas for blowing after the Al-Ti alloy block is completely melted, removing slag, and preserving heat for 20min; then cooling to 660 ℃, adding Zn blocks, introducing argon gas for blowing after the Zn blocks are completely melted, removing slag, and preserving heat for 20min; heating to 700 ℃ again, adding an Al-Ce alloy block, pressing the Al-Ce alloy block into the bottom, introducing argon for blowing after all the Al-Ce alloy block is melted, removing slag, and preserving heat for 25min; cooling to room temperature along with the furnace after heat preservation is finished, and obtaining a rough blank;
s3: performing electric spark processing on the rough blank obtained in the step S2 to obtain a plurality of alloy blocks with smaller sizes, putting the alloy blocks into a vacuum induction melting furnace, gradually increasing the heating power to 15kW, preserving heat for 20min, and casting to obtain a primary ingot;
s4: cutting the alloy ingot obtained in the step S3 into 130mm multiplied by 140mm multiplied by 12mm samples by utilizing line cutting, removing greasy dirt on the surface of the samples, and drying for later use;
s5: putting the sample obtained in the step S4 into a heat treatment furnace, heating to 400 ℃ and preserving heat for 1h;
s6: and (3) rapidly taking out the sample in the step (S5) for rolling, wherein the single pressing amount is not more than 10% and the total pressing amount is 50% by adopting a double-roller rolling mode, and cooling by water after rolling to obtain the high-strength high-damping Al-Zn eutectoid damping alloy, wherein the high-strength high-damping Al-Zn eutectoid damping alloy is required to be put into a furnace for heat preservation for 2min after each rolling.
Experimental example
Taking the alloy prepared in example 1 as an example, the performance of the high-strength high-damping Al-Zn eutectoid damping alloy will be described.
Two sets of parallel specimens, labeled #1 and #2, were cut from different locations of the alloy prepared in example 1. The structure observation is carried out on the alloy sample with the size of 10mm multiplied by 6mm by adopting a scanning electron microscope, the alloy consists of a multi-scale micro-nano-grade alpha+eta eutectoid structure, and the eutectoid size is about 4-6 mu m, as shown in figure 1. The microstructure of the Al-Zn eutectoid damping alloy is observed in an amplifying way by adopting a transmission electron microscope, and the eutectoid cell of the extruded alloy has three scales of micro-nano structures: the first is an equiaxed granular structure with a grain size of about 500-700 nm, as shown in figure 2; the second is a lamellar structure with a certain length-diameter ratio (about 4:1), and the particle size is about 40-150 nm, as shown in figure 3; the third is a nano-scale precipitation structure of eta-Zn in an alpha-Al matrix, and the size is about 10-20 nm, as shown in figure 4. The area percentages of the three scale micro-nano structures were about 20%,70% and 10%, respectively. Mechanical property test is carried out on the alloy Jin Shiyang by adopting an electronic universal tester, the room temperature stretching curves of two groups of parallel samples have good coincidence, and the tensile strength sigma of the two groups of parallel samples is b About 390MPa (the relevant literature reports that the tensile strength of Al-Zn based alloys is typically less than 300MPa. About 25.8% improvement over the comparative example) as shown in FIG. 5. Alloy testing with 35mm 10m 1mm size using dynamic thermo-mechanical analyzer (DMA Q800)The samples are subjected to damping performance test, the damping performance-strain amplitude curves of the two groups of parallel samples have good coincidence, the alloy has higher damping performance while obtaining high strength, and when the strain amplitude is 8 multiplied by 10 -4 The tan delta value was about 0.037 (about 85% improvement over the comparative example), as shown in fig. 6.
Two sets of parallel specimens, labeled #3 and #4, were cut from different locations of the alloy prepared in comparative example 1. The structure observation is carried out on an alloy sample with the size of 10mm multiplied by 6mm by adopting a scanning electron microscope, the alloy mainly comprises lamellar alpha+eta eutectoid, the eutectoid size is about 30-50 mu m, and the length-diameter ratio of alpha and eta sheets in the eutectoid is about 15:1, as shown in figure 7. Mechanical property test is carried out on the alloy Jin Shiyang by adopting an electronic universal tester, the room temperature stretching curves of two groups of parallel samples have good coincidence, and the tensile strength sigma of the two groups of parallel samples is b About 310MPa, as shown in FIG. 8; the damping performance test is carried out on alloy samples with the size of 35mm multiplied by 10m multiplied by 1mm by adopting a dynamic thermal mechanical analyzer (DMA Q800), the damping performance-strain amplitude curves of two groups of parallel samples have good coincidence, and when the strain amplitude is 8 multiplied by 10 -4 The tan delta value was about 0.02 as shown in fig. 9.
While specific embodiments of the invention have been described in detail in connection with the examples, it should not be construed as limiting the scope of protection of the patent. Various modifications and variations which may be made by those skilled in the art without the creative effort are within the scope of the patent described in the claims.
Claims (9)
1. The high-strength high-damping Al-Zn eutectoid damping alloy is characterized by comprising the following components in atom percent: 45-54 at.% of Al, 45-54 at.% of Zn, 0.05-0.5 at.% of Ce and 0.5-2 at.% of Ti.
2. The high-strength high-damping Al-Zn eutectoid damping alloy according to claim 1, comprising, in atomic percent, al 50at.%, zn 48.9at.%, ce 0.1at.% and Ti 1at.%.
3. The method for preparing the high-strength high-damping Al-Zn eutectoid damping alloy according to claim 1 or 2, which is characterized by comprising the following steps:
s1: preparing raw materials according to an alloy composition ratio, wherein the raw materials comprise an aluminum block, a zinc block, an Al-Ce alloy block and an Al-Ti alloy block, the mass ratio of Ce in the Al-Ce alloy block is 10%, and the mass ratio of Ti in the Al-Ti alloy block is 10%;
s2: heating the aluminum block to 700-800 ℃ and preserving heat until the aluminum block is completely melted, then adding an Al-Ti alloy block into the aluminum liquid, blowing to remove slag after the aluminum block is completely melted, preserving heat for 15-25 min, then cooling to 630-670 ℃, adding a zinc block, blowing to remove slag after the aluminum block is completely melted, preserving heat for 15-25 min, then heating to 700-750 ℃ again, adding an Al-Ce alloy block into the zinc block, blowing to remove slag after the aluminum block is completely melted, and then cooling to room temperature along with a furnace to obtain a rough blank;
s3: heating the rough blank obtained in the step S2 to be molten, preserving heat for 15-25 min, and casting to obtain a primary ingot;
s4: homogenizing the initial ingot obtained in the step S3, and then cooling to room temperature by water;
s5: and (3) performing hot extrusion on the cast ingot subjected to the S4 treatment, and then performing water cooling to room temperature to obtain the aluminum alloy.
4. A method of preparation according to claim 3, characterized in that: the speed of the two heating in the S2 is 3-6 ℃/min.
5. The method of manufacturing according to claim 4, wherein: the rate of the two heating-up in S2 is 4 ℃/min.
6. A method of preparation according to claim 3, characterized in that: s2, raising the final temperature of the aluminum block to 740 ℃, wherein the time of the first heat preservation is 20min; before zinc blocks are added, the system temperature is 660 ℃, and the second heat preservation time is 20min; the temperature of the system before adding the Al-Ce alloy block was 700 ℃.
7. A method of preparation according to claim 3, characterized in that: the homogenization treatment temperature in S4 is 350-400 ℃ and the treatment time is 18-22 h.
8. The method of manufacturing according to claim 7, wherein: the homogenization treatment temperature is 380 ℃ and the treatment time is 20 hours.
9. A method of preparation according to claim 3, characterized in that: the hot extrusion temperature in S5 is 285-375 ℃, the extrusion rate is 0.1-10 mm/S, and the extrusion ratio is 6-16.
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN117026029A (en) * | 2023-08-09 | 2023-11-10 | 仲恺农业工程学院 | High-strength high-damping aluminum-zinc bimetallic alloy and preparation method thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN117026029A (en) * | 2023-08-09 | 2023-11-10 | 仲恺农业工程学院 | High-strength high-damping aluminum-zinc bimetallic alloy and preparation method thereof |
| CN117026029B (en) * | 2023-08-09 | 2024-03-01 | 仲恺农业工程学院 | High-strength high-damping aluminum-zinc bimetallic alloy and preparation method thereof |
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