CN113981283B - Al (aluminum) 3 Ti-reinforced Al-Zn-based in-situ composite damping material and preparation method thereof - Google Patents
Al (aluminum) 3 Ti-reinforced Al-Zn-based in-situ composite damping material and preparation method thereof Download PDFInfo
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Abstract
The invention provides Al 3 The Ti-reinforced Al-Zn-based in-situ composite damping material comprises, by atomic percentage, 40-70at.% of Al, 40-70at.% of Zn, 0-1at.% of Ce and 0.5-10at.% of Ti. The composite damping material can effectively solve the problem of poor mechanical property of the existing damping material.
Description
Technical Field
The invention belongs to the technical field of alloy preparation, and particularly relates to Al 3 A Ti-reinforced Al-Zn-based in-situ composite damping material and a preparation method thereof.
Background
The development of damping materials is continuously improved along with the progress of modern industry, and nowadays, people not only require high speed, high precision and high efficiency for machinery, but also require that noise and vibration of the machinery during operation can be as small as possible. The traditional measures for vibration and noise reduction are realized by improving the mechanical rigidity and adding accessories, but the traditional measures can cause the increase of the mechanical weight and the design complexity. Therefore, people begin to research and develop vibration damping materials, the vibration damping materials convert vibration and noise into heat energy to be dissipated, the influence of the vibration and the noise can be reduced and prevented from the source, and Al-Zn-based vibration damping alloy in the vibration damping materials is widely concerned due to the advantages of good vibration damping property, low density, easy processing, low price and the like. There are studies showing that: the damping mechanism of Al-Zn-based alloys stems from phase interface slippage and viscous flow of grain boundaries. The alloy is subjected to external force to cause phase boundary and grain boundary slippage, and internal loss is generated in the slippage process. External forces can also cause stress concentration at grain boundaries, causing microscopic plastic deformation of the soft phase, resulting in dissipation of energy. Therefore, the damping performance of the alloy can be effectively improved by increasing the areas of the phase interface and the grain boundary. By adding rare earth Ce and other elements into the alloy as alterant, the effects of refining crystal grains and increasing the area of phase interface are achieved, thereby improving the damping performance of the alloy.
However, the mechanical properties of Al-Zn alloy are relatively poor, and especially the strength is relatively low, which limits the wider application of the alloy to a certain extent. Therefore, the improvement of the comprehensive performance of the Al-Zn base alloy, in particular the mechanical property thereof, has very important significance for the research, development and application of the alloy.
Disclosure of Invention
In order to solve the problems in the prior art, the invention provides Al 3 The Ti-reinforced Al-Zn-based in-situ composite damping material can effectively solve the problem of poor mechanical property of the existing damping material.
In order to achieve the purpose, the technical scheme adopted by the invention for solving the technical problems is as follows:
al (aluminum) 3 The Ti reinforced Al-Zn based in-situ composite damping material comprises, by atomic percentage, 40-70at.% of Al, 40-70at.% of Zn, 0-1at.% of Ce and 0.5-10at.% of Ti.
Further, al 49.9at.%, zn 49.5at.%, ce 0.1at.%, ti 0.5at.%, in atomic percent.
Further, al 49.9at.%, zn 49at.%, ce 0.1at.%, ti 1at.%, in atomic percent.
Al mentioned above 3 The preparation method of the Ti-reinforced Al-Zn-based in-situ composite damping material comprises the following steps:
(1) Weighing an aluminum block, a zinc block, an Al-Ce alloy block and an Al-Ti alloy block;
(2) Heating the aluminum block to 750-800 ℃, preserving heat until the aluminum block is completely melted, adding an Al-Ti alloy block into the aluminum block, blowing gas to remove slag after the aluminum block is completely melted, preserving heat, then cooling to 630-670 ℃, continuing to add a zinc block into the aluminum block, blowing gas to remove slag after the aluminum block is completely melted, preserving heat, then heating again to 700-750 ℃, adding an Al-Ce alloy block into the aluminum block, blowing gas to remove slag after the aluminum block is completely melted, and preserving heat;
(3) Electromagnetically stirring the molten metal in the step (2), preserving heat, and cooling to room temperature along with the furnace to obtain a metal ingot;
(4) Processing and cutting the metal cast ingot in the step (3) to obtain a sample, heating the sample to 400-420 ℃, preserving heat for 1h, taking out the sample, and rolling to obtain a rolled sample;
(5) Keeping the temperature of the rolled sample at 360-400 ℃ for 0-10h, then carrying out solution treatment, then carrying out water-cooling quenching, then keeping the temperature at 100-200 ℃ for 0-10h, carrying out aging treatment, and then carrying out water-cooling quenching to obtain the steel.
Further, in the step (1), the mass ratio of Ce in the Al-Ce alloy block is 10%, the mass ratio of Ti in the Al-Ti alloy block is 10%, and the purities of the Al-Ce alloy block and the Al-Ti alloy block are both more than 99 wt%.
Further, in the step (2), the temperature of the aluminum block is increased at a speed of 4 ℃/min.
Further, the heat preservation time in the step (2) is 20-25min.
The beneficial effects produced by the invention are as follows:
1. the invention adds Ti element into Al-Zn-Ce alloy to obtain the Al-containing alloy 3 In-situ composite structure of Ti intermetallic compound, refining alloy structure by adding Ti element, al 3 Ti is a hard intermetallic compound and can be used as a strengthening phase to exist in a matrix, so that the mechanical property of the in-situ composite damping material is obviously improved under the condition of ensuring excellent damping property.
2. According to the invention, the structure, damping performance and mechanical property of the composite damping material are regulated, controlled and optimized by adjusting the content of Ti and the solid solution aging process, so that the composite damping material with excellent comprehensive performance is obtained.
3. The preparation method is simple, easy to operate, low in production cost and wide in application prospect.
Drawings
FIG. 1 shows Al in example 1 3 OM photo of Ti enhanced Al-Zn based in-situ composite damping material;
FIG. 2 is a schematic view of an embodimentAl in example 2 3 OM photo of Ti enhanced Al-Zn based in-situ composite damping material;
FIG. 3 is an OM photograph of the Al-Zn based damping alloy in the comparative example;
FIG. 4 shows Al in example 1 3 The damping performance-strain amplitude curve of the Ti-reinforced Al-Zn-based in-situ composite damping material;
FIG. 5 shows Al in example 2 3 The damping performance-strain amplitude curve of the Ti-reinforced Al-Zn-based in-situ composite damping material;
FIG. 6 is a damping performance-strain amplitude curve of the Al-Zn-based damping alloy in the comparative example;
FIG. 7 shows Al in example 1 3 The room temperature tensile curve of the Ti-reinforced Al-Zn-based in-situ composite damping material;
FIG. 8 shows Al in example 2 3 The room temperature tensile curve of the Ti-reinforced Al-Zn-based in-situ composite damping material;
FIG. 9 is a room temperature tensile curve of the Al-Zn based damping alloy in the comparative example.
Detailed Description
The following detailed description of embodiments of the invention refers to the accompanying drawings.
Example 1
Al 3 The preparation method of the Ti-reinforced Al-Zn-based in-situ composite damping material comprises the following steps:
(1) Weighing a simple substance Al block, a simple substance Zn block, an Al-Ce alloy block and an Al-Ti alloy block according to the component proportion of 49.9at.% Al, 49.5at.% Zn, 0.1at.% 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%;
(2) Putting the aluminum block into a crucible of a well-type resistance furnace, heating the aluminum block to 740 ℃ at the heating rate of 4 ℃/min, and preserving heat until the aluminum block is completely melted; adding Al-Ti alloy blocks, introducing argon gas for blowing and deslagging after the Al-Ti alloy blocks are completely molten, and keeping the temperature for 20 minutes; then cooling to 660 ℃, adding Zn blocks, introducing argon gas for blowing and deslagging after the Zn blocks are completely melted, and keeping the temperature for 20 minutes; raising the temperature to 700 ℃ again, adding the Al-Ce alloy block, pressing the Al-Ce alloy block into the bottom, introducing argon gas for blowing and deslagging after the Al-Ce alloy block is completely melted, and keeping the temperature for 25 minutes;
(3) Transferring the molten metal in the step (2) to an electromagnetic stirring furnace, starting electromagnetic stirring and preserving heat for 10 minutes; cooling to room temperature along with the furnace after the heat preservation is finished (when the temperature is reduced to 400 ℃, closing the electromagnetic stirring), and obtaining the required alloy ingot;
(4) Performing electric spark machining on the alloy cast ingot in the step (3) to obtain a sample with the size of 130mm multiplied by 12mm, putting the cast-state sample into a heat treatment furnace for heating, keeping the temperature for 1 hour when the temperature is raised to 400 ℃, taking out the sample after the heat preservation is finished, and performing multi-pass rolling (the total pressing amount is 60%) on the sample to obtain a required rolled-state sample;
(5) Preserving the temperature of the rolled sample in the step (4) for 4 hours at 380 ℃ for solution treatment, and then carrying out water-cooling quenching;
(6) Preserving the heat of the sample in the step (5) at 150 ℃ for 2h for aging treatment, then carrying out water-cooling quenching, and finally obtaining the required Al 3 Ti reinforced Al-Zn based in-situ composite damping material.
Observing the structure of an alloy sample with the size of 10mm multiplied by 10m multiplied by 6mm by adopting an optical metallographic microscope, wherein the alloy structure is formed by uniformly distributed Al 3 Ti intermetallic compound mass, and beta dendrite with compositional segregation, as shown in fig. 1. Further analysis revealed that during subsequent cooling, the dendrite β phase undergoes a β → α + η eutectoid transformation (eutectoid organization into a fine lamellar structure with a two-phase lamellar spacing of about several hundred nanometers). Compared with the eutectoid structure in the comparative example, the sizes of α and η in the eutectoid structure of example 1 become smaller, and the crystal grains are refined; adopting an electronic universal mechanical testing machine to test the mechanical property of the alloy sample, and the tensile strength sigma of the alloy sample b About 280MPa, elongation about 18% (about 4.2% and 50% improvement compared to the comparative example), as shown in FIG. 4; the hardness of the alloy specimen measured using a model HBRV-187.5 blovin hardness tester was about 85.24HBW (see table 1, which is an improvement of about 7% over the comparative example); the alloy sample with the size of 1.5mm multiplied by 50mm is subjected to damping performance test by adopting a multifunctional inverted torsion pendulum internal friction tester, and when the strain amplitude is 10 -3 When it is Q -1 A value of about 0.035 (an improvement of about 119% compared to the comparative example) as shown in FIG. 7.
Example 2
Al (aluminum) 3 The preparation method of the Ti-reinforced Al-Zn-based in-situ composite damping material comprises the following steps:
(1) Weighing a simple substance Al block, a simple substance Zn block, an Al-Ce alloy block and an Al-Ti alloy block according to the component proportion of 49.9at.% Al, 49at.% 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%;
(2) Putting the aluminum block into a crucible of a well-type resistance furnace, heating the aluminum block to 740 ℃ at the heating rate of 4 ℃/min, and preserving heat until the aluminum block is completely melted; adding Al-Ti alloy blocks, introducing argon gas for blowing and deslagging after the Al-Ti alloy blocks are completely molten, and keeping the temperature for 20 minutes; then cooling to 660 ℃, adding Zn blocks, introducing argon gas for blowing and deslagging after the Zn blocks are completely melted, and keeping the temperature for 20 minutes; raising the temperature to 700 ℃ again, adding the Al-Ce alloy block, pressing the Al-Ce alloy block into the bottom, introducing argon gas for blowing and deslagging after the Al-Ce alloy block is completely melted, and keeping the temperature for 25 minutes;
(3) Transferring the molten metal into an electromagnetic stirring furnace, starting electromagnetic stirring and preserving heat for 10 minutes; cooling to room temperature along with the furnace after the heat preservation is finished (when the temperature is reduced to 400 ℃, closing the electromagnetic stirring), and obtaining the required alloy ingot;
(4) Performing electric spark machining on the alloy cast ingot in the step (3) to obtain a sample with the size of 130mm multiplied by 12mm, putting the cast-state sample into a heat treatment furnace for heating, preserving heat for 1 hour when the temperature is raised to 400 ℃, taking out the sample after the heat preservation is finished, and performing multi-pass rolling on the sample (the total pressing amount is 60%) to obtain a required rolled-state sample;
(5) Preserving the temperature of the rolled sample in the step (4) for 4 hours at 380 ℃ for solution treatment, and then carrying out water-cooling quenching;
(6) Preserving the heat of the sample in the step (5) at 150 ℃ for 2h for aging treatment, then carrying out water-cooling quenching, and finally obtaining the required Al 3 Ti reinforced Al-Zn based in-situ composite damping material.
Using optical goldThe alloy sample with the size of 10mm multiplied by 6mm is observed by a phase microscope, and the alloy structure is evenly distributed with Al 3 Ti intermetallic compound mass, and beta dendrite with compositional segregation, as shown in fig. 2. Further analysis revealed that during subsequent cooling, the dendrite β phase undergoes a β → α + η eutectoid transformation (eutectoid organization into a fine lamellar structure with a two-phase lamellar spacing of about several hundred nanometers). Compared with the eutectoid structure in the comparative example, the sizes of α and η in the eutectoid structure of example 1 become smaller, and the crystal grains are refined; mechanical property test is carried out on the alloy sample by adopting an electronic universal mechanical testing machine, and the tensile strength sigma of the alloy sample is b About 347MPa with an elongation of about 19% (an improvement of about 26.6% and 58.3%, respectively, compared to the comparative example), as shown in fig. 5; the hardness of the alloy specimen as measured by a Brookfield hardness tester type HBRV-187.5 is about 91.9HBW (see Table 1, which is an improvement of about 15.4% over the comparative example); the alloy sample with the size of 1.5mm multiplied by 50mm is subjected to damping performance test by adopting a multifunctional inverted torsion pendulum internal consumption instrument, and when the strain amplitude is 10 -3 When it is Q -1 The value was about 0.034 (an improvement of about 113% compared to the comparative example), as shown in fig. 8.
Comparative example
An Al-Zn-based damping alloy and a preparation method thereof comprise the following steps:
(1) Weighing simple substance Al blocks, simple substance Zn blocks and Al-Ce alloy blocks according to the component proportion of 49.9at.% Al, 50at.% Zn and 0.1at.% Ce, wherein the purity of each raw material is more than 99wt.%, and the mass ratio of Ce in the Al-Ce alloy blocks is 10%;
(2) Putting the aluminum block into a crucible of a well-type resistance furnace, heating the aluminum block to 770 ℃ at the heating rate of 4 ℃/min, and preserving heat until the aluminum block is completely melted; then cooling to 660 ℃, adding Zn blocks, introducing argon gas for blowing and deslagging after the Zn blocks are completely melted, and keeping the temperature for 20 minutes; raising the temperature to 700 ℃ again, adding the Al-Ce alloy block, pressing the Al-Ce alloy block into the bottom, introducing argon gas for blowing and deslagging after the Al-Ce alloy block is completely melted, and keeping the temperature for 25 minutes;
(3) Transferring the molten metal into an electromagnetic stirring furnace, starting electromagnetic stirring and preserving heat for 10 minutes; cooling to room temperature along with the furnace after the heat preservation is finished (when the temperature is reduced to 400 ℃, closing the electromagnetic stirring), and obtaining the required alloy ingot;
(4) Performing electric spark machining on the alloy cast ingot in the step (3) to obtain a sample with the size of 130mm multiplied by 12mm, putting the cast-state sample into a heat treatment furnace for heating, keeping the temperature for 1 hour when the temperature is raised to 400 ℃, taking out the sample after the heat preservation is finished, and performing multi-pass rolling (the total pressing amount is 60%) on the sample to obtain a required rolled-state sample;
(5) Preserving the temperature of the rolled sample in the step (4) at 380 ℃ for 4h for solution treatment, and then performing water-cooling quenching;
(6) And (3) preserving the temperature of the sample in the step (5) for 2h at 150 ℃ for aging treatment, and then carrying out water-cooling quenching to finally obtain the required Al-Zn-Ce damping alloy.
An alloy sample having dimensions of 10mm × 10mm × 6mm was subjected to structure observation using an optical metallographic microscope, and the alloy structure was mainly composed of β dendrites having component segregation, as shown in fig. 3. Further analysis shows that during the subsequent cooling process, the beta phase of the dendrite undergoes beta → alpha + eta eutectoid transformation (eutectoid structure is a fine lamellar structure, and the distance between two lamellar layers is about hundreds of nanometers); mechanical property test is carried out on the alloy sample by adopting an electronic universal mechanical testing machine, and the tensile strength sigma of the alloy sample is b About 274MPa, elongation about 12%, as shown in FIG. 6; the alloy specimen hardness was about 79.64HBW as measured using a Brookfield hardness tester model HBRV-187.5 (see Table 1); the alloy sample with the size of 1.5mm multiplied by 50mm is subjected to damping performance test by adopting a multifunctional inverted torsion pendulum internal consumption instrument, and when the strain amplitude is 10 -3 When it is Q -1 The value is about 0.016 as shown in fig. 9.
Table 1:
| alloy (I) | Hardness (HBW) |
| Example 1 | 85.24 |
| Example 2 | 91.90 |
| Comparative example | 79.64 |
Claims (2)
1. Al 3 The Ti-reinforced Al-Zn-based in-situ composite damping material is characterized by comprising 49.9at.% of Al, 49.5at.% of Zn, 0.1at.% of Ce, 0.5at.% of Ti or 49.9at.% of Al, 49at.% of Zn, 0.1at.% of Ce and 1at.% of Ti in atomic percentage;
the preparation method comprises the following steps:
(1) Weighing an aluminum block, a zinc block, an Al-Ce alloy block and an Al-Ti alloy block;
(2) Heating the aluminum block to 750-800 ℃ at the speed of 4 ℃/min, preserving heat until the aluminum block is completely melted, adding an Al-Ti alloy block into the aluminum block, blowing gas for deslagging after the aluminum block is completely melted, preserving heat for 20-25min, then cooling to 630-670 ℃, continuing adding a zinc block into the aluminum block, blowing gas for deslagging after the aluminum block is completely melted, preserving heat, then heating again to 700-750 ℃, adding an Al-Ce alloy block into the aluminum block, blowing gas for deslagging after the aluminum block is completely melted, and preserving heat;
(3) Electromagnetically stirring the molten metal in the step (2), preserving heat, and cooling to room temperature along with a furnace to obtain a metal ingot;
(4) Processing and cutting the metal cast ingot in the step (3) to obtain a sample, heating the sample to 400-420 ℃, preserving heat for 1h, taking out the sample, and rolling to obtain a rolled sample;
(5) Keeping the temperature of the rolled sample at 360-400 ℃ for 0-10h, then carrying out solution treatment, then carrying out water-cooling quenching, then keeping the temperature at 100-200 ℃ for 0-10h, carrying out aging treatment, and then carrying out water-cooling quenching to obtain the steel.
2. Al according to claim 1 3 The Ti-reinforced Al-Zn-based in-situ composite damping material is characterized in that in the step (1), the mass proportion of Ce in the Al-Ce alloy block is 10%, the mass proportion of Ti in the Al-Ti alloy block is 10%, and the purities of the Al-Ce alloy block and the Al-Ti alloy block are both more than 99 wt%.
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| JPS607018B2 (en) * | 1979-08-27 | 1985-02-21 | 財団法人電気磁気材料研究所 | Aluminum-based vibration absorbing alloy with large damping capacity and its manufacturing method |
| CN1031862A (en) * | 1987-09-05 | 1989-03-22 | 东南大学 | High abrasion, anti-corrosion, high damping aluminium-zinc cast alloy |
| CN1098934C (en) * | 1998-12-25 | 2003-01-15 | 西南交通大学 | Zinc-aluminum alloy preparation process |
| CN101736181A (en) * | 2008-11-19 | 2010-06-16 | 沈阳龙实合金有限公司 | High aluminum zinc-based bearing alloy and preparation method thereof |
| CN104711469A (en) * | 2014-10-20 | 2015-06-17 | 西南交通大学 | Heterogeneous high damping magnesium alloy |
| CN106399755B (en) * | 2016-12-12 | 2018-05-04 | 福州大学 | A kind of environment-friendly type zinc-aluminium damping alloy and preparation method thereof |
| CN109022966A (en) * | 2018-09-20 | 2018-12-18 | 重庆理工大学 | A kind of rare earth Er contained and Ce element damping alumin(i)um zinc alloy and preparation method thereof |
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