CN115896559A - High-thermal-conductivity aluminum alloy and preparation method thereof - Google Patents
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Abstract
The invention belongs to the field of aluminum alloy preparation, and particularly relates to a high-thermal-conductivity aluminum alloy and a preparation method thereof, wherein the high-thermal-conductivity aluminum alloy comprises the following components, by mass, 1.5-2.5% of Si, 0.35-0.55% of Fe, 0.05-0.06% of Mg, 0.35-0.6% of Mn, 0.006-0.025% of Sr0.4-0.6% of rare earth metal, 0.1-0.15% of Sc and the balance Al.
Description
Technical Field
The invention belongs to the technical field of aluminum alloy, and particularly relates to a high-thermal-conductivity aluminum alloy and a preparation method thereof.
Background
With the arrival of the 5G communication era, the chip integration of electronic products and communication equipment is improved, the equipment power is increased, the heat productivity is increased, and the heat dissipation capacity of the equipment per unit volume is increased, which puts higher requirements on the heat conduction performance of the material to ensure the service life of the product and the working stability. Pure aluminum has good thermal conductivity, with a room temperature thermal conductivity of about 237W/(m · K), second only to copper (385W/(m · K)) in metallic materials. However, the strength of pure aluminum is too low, only 69MPa, which cannot meet the requirements of industrial production application, and the strength of pure aluminum needs to be improved by alloying, but the addition of alloying elements can significantly reduce the heat conducting performance of the material. The reason is that the alloying elements strengthen the aluminum alloy mainly in the form of solid solution atoms, generated mesophases, or precipitation strengthening phases in the Al matrix. According to the microscopic mechanism analysis of metal heat conduction, due to the existence of structural defects such as vacancies, dislocations and the like and precipitated phases in crystals, the crystal lattice distortion of the alloy can be caused, the probability of scattering free electrons is increased, the number of effective electrons participating in heat transfer is reduced, the mean free path of the heat transfer electrons is limited, and therefore the heat conduction performance of the alloy is reduced.
The content of Si in the ENAC-43400 die-casting alloy which is widely applied to the production of communication heat dissipation devices at present is 9.5 to 11.0 percent, and the alloy has excellent casting fluidity and good mechanical property. However, a large amount of coarse lath-shaped primary crystal silicon and needle-shaped eutectic crystal silicon exist in the ENAC-43400 alloy structure, the Al matrix is seriously cut, and the material is remarkably reduced
The performance, the thermal conductivity of which is only 130W/(m.K), is far less than that of pure aluminum, which limits further development and application of Al-Si alloy to a certain extent. At present, al-Si alloy die castings can meet the requirement of heat conductivity after heat treatment, but uncontrollable factors are more in the heat treatment process, the die castings are easy to deform, and the cost of the heat treatment process is high. Therefore, how to solve the problem of mutual restriction among strengthening, heat-conducting property and cost of the aluminum alloy, on the premise of ensuring the mechanical property of the cast aluminum alloy, the heat-conducting property of the cast aluminum alloy is greatly improved, and the high-heat-conducting die-casting aluminum alloy which has the characteristics of good fluidity, good demolding property, low manufacturing cost and the like is obtained, which becomes a key technical problem to be solved urgently.
Disclosure of Invention
The invention aims to provide a high-thermal-conductivity aluminum alloy and a preparation method thereof, the Si content in the aluminum alloy is controlled to be about 2%, a small amount of Mg and Sc are added as trace strengthening elements in an auxiliary manner, rare earth metal elements are used as modification elements, a low-Si cast alloy with excellent thermal conductivity, excellent mechanical property and casting fluidity is obtained, and meanwhile, the microstructure characteristics of grain combination refinement, grain boundary precipitated phase dispersion distribution, grain boundary no-precipitate phase width narrowing and the like after Sc and Sr microalloying are also beneficial to reducing the corrosion sensitivity of the aluminum alloy.
The technical purpose of the invention is realized by the following technical scheme: the high heat conductivity aluminum alloy comprises, by mass, 1.5-2.5% of Si, 0.35-0.55% of Fe, 0.05-0.06% of Mg, 0.35-0.6% of Mn, 0.006-0.025% of Sr0.4-0.6% of rare earth metal, 0.1-0.15% of Sc, and the balance of Al.
The invention is further provided with: the rare earth element metal is one of Er or Yb.
The invention is further configured as follows: also comprises the following components: and (4) graphite filler.
A preparation method of a high-thermal-conductivity aluminum alloy comprises the following preparation steps:
step one, heating a smelting furnace to 750-760 ℃, putting raw materials into the smelting furnace to melt so as to obtain molten aluminum, melting the molten aluminum into electromagnetic stirring and melting, stirring the molten aluminum alloy through a magnetic field penetrating through the furnace bottom, and performing steps of deslagging, online degassing, filtering and the like;
secondly, adding a certain mass of graphite filler into a prepressing die, applying a certain pressure to form a prepressing block, and heating the die and the prepressing block to 400-500 ℃;
and step three, quickly pouring the molten aluminum alloy in the step one into the preheated mold in the step two, then applying pressure to enable the molten aluminum alloy to be filled into the pores of the prepressing block, and demoulding after cooling to obtain the high-thermal-conductivity aluminum alloy.
The invention is further provided with: the pressure in the third step is 100-120MPa, and the pressure maintaining time is 60-120s. .
The invention is further provided with: the mass ratio of the graphite filler to the aluminum alloy melt is 0.3-0.5:1.
the invention is further provided with: the graphite filler is a mixture of graphite flakes and silicon particles.
The invention is further provided with: the mass fraction of the graphite flakes and the silicon particles is 2.5-1.
The invention is further configured as follows: the online degassing is degassing in a furnace, the temperature of the furnace is adjusted to 730-740 ℃ during the degassing in the furnace, then inert gas with the pressure of 0.2-0.3Mpa is input into the aluminum liquid, wherein the degassing time is 3-5min, and the height of bubbles formed on the top of the aluminum liquid is lower than 10cm.
The beneficial effects of the invention are:
1. according to the invention, the Si content in the aluminum alloy is controlled to be about 2%, a small amount of Mg and Sc are added as trace strengthening elements in an auxiliary manner, and rare earth metal elements are used as modification elements, so that the low-Si cast alloy with excellent heat conductivity, excellent mechanical property and casting fluidity is obtained, and meanwhile, the microstructure characteristics of grain combination refinement, grain boundary precipitation phase dispersion distribution, grain boundary non-precipitation phase width narrowing and the like after the Sc and Sr micro-alloy are also beneficial to reducing the corrosion sensitivity of the aluminum alloy.
2. In the present invention, the addition of Sc lowers the corrosion potential of the aluminum alloy and also improves the weldability of the aluminum alloy. Al is formed in a welding seam area after the Sc-added aluminum alloy is welded 3 And when the Sc content is higher than that of the eutectic component, the crystal grains in the welding nucleus area can be obviously refined to form fine equiaxed crystal grains, the tendency of generating cracks during solidification is reduced, the mechanical property, the corrosion property and the like of a welding line are improved, and therefore, the welding connection of the Sc microalloyed alloy is realizedThe alloy head not only has high strength, but also has better corrosion resistance and fatigue resistance, but the price of the metal Sc is higher, so the invention adopts other rare earth metals with lower price to replace the added metal Sc, such as Er or Yb. When the alloy is solidified, most Er is gathered at the front edge of a solid-liquid interface, so that the content of Er near the interface is very high and exceeds the eutectic point component, and primary Al is directly precipitated from the alloy melt 3 Er particles due to Al 3 The Er has very similar structure with the Al matrix, has small mismatching degree, has better interface coherent characteristic with the Al matrix, and is preferentially separated out when the alloy is solidified, so that the Al is 3 The Er particles can become a good heterogeneous nucleation core, thereby having a strong effect on grain refinement of the alloy. In addition, the addition of Er can inhibit recrystallization, thereby improving the thermal stability of the alloy, and in addition, fine and dispersed Al is precipitated in the alloy during the heat treatment process 3 The Er phase can generate dispersion strengthening, second phase strengthening, substructure strengthening and the like, and the mechanical property of the alloy is obviously improved.
3. After the Er or Yb is added into the aluminum alloy, the Er or Yb is obviously refined, eutectic Si, al-Fe-Si phases and Al-Si phases in the alloy are also obviously changed, the needle-shaped morphology of the alloy is changed into a short rod shape, sharp edges and corners are smoother, and compounds at crystal boundaries are uniformly distributed, so that the cutting action of the needle-shaped compounds on a matrix in the original alloy is reduced, and the strength and the hardness of the alloy are greatly improved. Er or Yb has active chemical property and the function of reducing surface tension, thus modifying the needle-shaped eutectic silicon in the alloy matrix and improving the distribution form of the phases in the matrix.
4. The invention has the advantages that after the rare earth elements are added, the effects of deoxidation, desulfurization and hydrogen absorption are obviously improved, because the rare earth elements can form rare earth oxides or rare earth sulfides with oxygen or sulfur in the metal liquid, the rare earth elements can also form compounds with metal impurities with low melting point of air pressure, so that the rare earth elements float to form slag in the smelting process, the rare earth has larger adsorption capacity to hydrogen, can adsorb and dissolve a large amount of hydrogen, the melting point of the compounds of the rare earth and the hydrogen is higher, and the compounds are dispersed and distributed in the aluminum liquid for summary, the hydrogen formed by the compounds can not be aggregated to form bubbles, the hydrogen content and the pinhole rate in the aluminum alloy are greatly reduced, in addition, because the rare earth elements can react with the hydrogen to generate stable rare earth hydrides, the content of free hydrogen in the aluminum liquid can be reduced, and the porosity of the aluminum alloy is further reduced.
5. The invention compounds the aluminum alloy and the graphite filler, the graphite reinforced composite material has higher thermal conductivity, the graphite sheets have higher graphitization degree and preferred crystal orientation and have higher thermal conductivity, but the compound molding of the graphite sheets and the aluminum alloy matrix has great difficulty, because aluminum atoms are diffused and received resistance, simultaneously, under pressure, the graphite sheets can be mutually overlapped, gaps among the graphite sheets can be pressed, thus the infiltration of aluminum alloy solution can not be realized.
Detailed Description
The technical solutions in the embodiments will be clearly and completely described below. It is to be understood that the described embodiments are merely a few embodiments of the invention, and not all embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments of the present invention without inventive step, shall fall within the scope of protection of the present invention.
Comparative example 1
The high heat conductivity aluminum alloy comprises, by mass, 1.5-2.5% of Si, 0.35-0.55% of Fe, 0.05-0.06% of Mg, 0.35-0.6% of Mnand the balance of Al.
The preparation method comprises the following preparation steps:
step one, heating a smelting furnace to 750-760 ℃, putting raw materials into the smelting furnace to melt so as to obtain aluminum liquid, melting the aluminum liquid into electromagnetic stirring and melting, and stirring the aluminum liquid by penetrating a magnetic field through a furnace bottom;
and step two, deslagging the aluminum liquid obtained in the step one, degassing on line, filtering and casting.
Example 1
The high heat conductivity aluminum alloy comprises, by mass, 1.5-2.5% of Si, 0.35-0.55% of Fe, 0.05-0.06% of Mg, 0.35-0.6% of Mn, 0.006-0.025% of Sr0.1-0.15% of Sc, and the balance of Al.
The preparation method comprises the following preparation steps:
step one, heating a smelting furnace to 750-760 ℃, putting raw materials into the smelting furnace to melt so as to obtain aluminum liquid, melting the aluminum liquid into electromagnetic stirring and melting, and stirring the aluminum liquid by penetrating a magnetic field through a furnace bottom;
and step two, deslagging the aluminum liquid obtained in the step one, degassing on line, filtering and casting.
Example 2
The high heat conductivity aluminum alloy comprises, by mass, 1.5-2.5% of Si, 0.35-0.55% of Fe, 0.05-0.06% of Mg, 0.35-0.6% of Mn0.4-0.6% of rare earth metal, and the balance of Al.
The preparation method comprises the following preparation steps:
step one, heating a smelting furnace to 750-760 ℃, putting raw materials into the smelting furnace to melt so as to obtain aluminum liquid, melting the aluminum liquid into electromagnetic stirring and melting, and stirring the aluminum liquid by penetrating a magnetic field through a furnace bottom;
and step two, deslagging the aluminum liquid obtained in the step one, degassing on line, filtering and casting.
Example 3
The high heat conductivity aluminum alloy comprises, by mass, 1.5-2.5% of Si, 0.35-0.55% of Fe, 0.05-0.06% of Mg, 0.35-0.6% of Mn, 0.006-0.025% of Sr0.4-0.6% of rare earth metal, 0.1-0.15% of Sc, and the balance of Al.
The preparation method comprises the following preparation steps:
step one, heating a smelting furnace to 750-760 ℃, putting raw materials into the smelting furnace to melt so as to obtain aluminum liquid, melting the aluminum liquid into electromagnetic stirring and melting, and stirring the aluminum liquid by penetrating a magnetic field through a furnace bottom;
and step two, deslagging, online degassing, filtering and casting the molten aluminum obtained in the step one.
Example 4
The high heat conductivity aluminum alloy comprises, by mass, 1.5-2.5% of Si, 0.35-0.55% of Fe, 0.05-0.06% of Mg, 0.35-0.6% of Mn0.006-0.025% of Sr0.006-0.6% of rare earth metal, 0.1-0.15% of Sc and the balance Al.
The preparation method comprises the following preparation steps:
step one, heating a smelting furnace to 750-760 ℃, adding raw materials to melt to obtain molten aluminum, melting the molten aluminum into electromagnetic stirring and melting, stirring the molten aluminum alloy by penetrating a magnetic field through a furnace bottom, and performing deslagging, online degassing, filtering and other steps;
secondly, adding a mixture of graphite flakes and silicon particles with certain mass into a prepressing die, then applying certain pressure to form a prepressing block, and then heating the die and the prepressing block to 400-500 ℃;
and step three, quickly pouring the molten aluminum alloy in the step one into the preheated mold in the step two, then applying pressure to enable the molten aluminum alloy to be filled into the pores of the pre-pressing block, and demoulding after cooling to obtain the high-thermal-conductivity aluminum alloy.
Exfoliation corrosion testing: and respectively placing the prepared aluminum alloy into beakers containing corrosive liquid, then hermetically placing the beakers into a constant-temperature water bath kettle, preserving the heat for 25 ℃, taking out the beakers after soaking for 10 hours, cleaning and drying the beakers, and observing the corrosion morphology of the surface of each aluminum alloy by using a scanning electron microscope.
The aluminum alloys obtained in comparative example 1 and examples 1 to 4 were subjected to property testing to obtain respective test data shown in Table 1.
As can be seen from Table 1, compared with comparative example 1, in example 1, the corrosion morphology of the alloy is not obviously changed due to the addition of Sc metal, and the microstructure characteristics of grain combination refinement, grain boundary precipitation phase dispersion distribution, grain boundary no-precipitation phase width narrowing and the like of the Sc and Sr micro-alloys also contribute to reducing the corrosion sensitivity of the aluminum alloy. Compared with the comparative example 1, the rare earth element is added in the example 2, the strength and the hardness of the alloy are greatly improved, and the thermal conductivity of the aluminum alloy is obviously improved, compared with the example 4 and the example 3, the example 4 carries out the compounding of a small amount of the aluminum alloy and the graphite filler, so that the aluminum alloy can have higher thermal conductivity. According to the invention, the Si content in the aluminum alloy is controlled to be about 2%, a small amount of Mg and Sc are added as trace strengthening elements in an auxiliary manner, and rare earth metal elements are used as modification elements, so that the low-Si cast alloy with excellent heat conductivity, excellent mechanical property and casting fluidity is obtained, and meanwhile, the microstructure characteristics of grain combination refinement, grain boundary precipitation phase dispersion distribution, grain boundary non-precipitation phase width narrowing and the like after the Sc and Sr micro-alloy are also beneficial to reducing the corrosion sensitivity of the aluminum alloy.
Claims (9)
1. A high heat conduction aluminum alloy is characterized in that: the alloy comprises, by mass, 1.5-2.5% of Si, 0.35-0.55% of Fe0.05-0.06% of Mg, 0.35-0.6% of Mn0.006-0.025% of Sr0.4-0.6% of rare earth metal, 0.1-0.15% of Sc, and the balance of Al.
2. The aluminum alloy with high thermal conductivity as claimed in claim 1, wherein: the rare earth element metal is one of Er or Yb.
3. The aluminum alloy with high thermal conductivity as claimed in claim 1, wherein: also comprises the following components: and (3) graphite filler.
4. The method for preparing the high-thermal-conductivity aluminum alloy according to claim 1, wherein the method comprises the following steps: the preparation method comprises the following preparation steps:
step one, heating a smelting furnace to 750-760 ℃, adding raw materials to melt to obtain molten aluminum, melting the molten aluminum into electromagnetic stirring and melting, stirring the molten aluminum alloy by penetrating a magnetic field through a furnace bottom, and performing deslagging, online degassing, filtering and other steps;
secondly, adding a certain mass of graphite filler into a prepressing die, applying a certain pressure to form a prepressing block, and heating the die and the prepressing block to 400-500 ℃;
and step three, quickly pouring the molten aluminum alloy in the step one into the preheated mold in the step two, then applying pressure to enable the molten aluminum alloy to be filled into the pores of the prepressing block, and demoulding after cooling to obtain the high-thermal-conductivity aluminum alloy.
5. The method for preparing the high-thermal-conductivity aluminum alloy according to claim 4, wherein the method comprises the following steps: the pressure in the third step is 100-120MPa, and the pressure maintaining time is 60-120s.
6. The preparation method of the high-thermal-conductivity aluminum alloy according to claim 4, characterized by comprising the following steps: the mass ratio of the graphite filler to the aluminum alloy melt is 0.3-0.5:1.
7. the method for preparing the high-thermal-conductivity aluminum alloy according to claim 4, wherein the method comprises the following steps: the graphite filler is a mixture of graphite flakes and silicon particles.
8. The method for preparing the high-thermal-conductivity aluminum alloy according to claim 7, wherein the method comprises the following steps: the mass fraction of the graphite flakes and the silicon particles is 2.5-1.
9. The method for preparing the high-thermal-conductivity aluminum alloy according to claim 4, wherein the method comprises the following steps: the online degassing is degassing in a furnace, the temperature of the furnace is adjusted to 730-740 ℃ during the degassing in the furnace, then inert gas with the pressure of 0.2-0.3Mpa is input into the aluminum liquid, wherein the degassing time is 3-5min, and the height of bubbles formed on the top of the aluminum liquid is lower than 10cm.
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Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103343265A (en) * | 2013-07-24 | 2013-10-09 | 上海交通大学 | Aluminum matrix composite with low expansion and high thermal conductivity reinforced by mixing graphite and silicon |
| CN103343266A (en) * | 2013-07-24 | 2013-10-09 | 上海交通大学 | High-thermal-conductivity graphite-high silicon aluminium-based composite material and preparation process for same |
| CN105734333A (en) * | 2016-03-10 | 2016-07-06 | 西北工业大学 | Heat conducting graphite/low-silicon/aluminium base composite and preparation method thereof |
| CN110016594A (en) * | 2019-05-07 | 2019-07-16 | 中铝广西崇左稀钪新材料科技有限公司 | A kind of die-casting rare earth aluminum alloy materials and preparation method thereof with high heat conductance |
| CN115161520A (en) * | 2022-06-07 | 2022-10-11 | 湖北新金洋资源股份公司 | High-strength and high-toughness heat-treatment-free casting aluminum alloy and preparation process thereof |
-
2022
- 2022-12-01 CN CN202211532100.XA patent/CN115896559A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103343265A (en) * | 2013-07-24 | 2013-10-09 | 上海交通大学 | Aluminum matrix composite with low expansion and high thermal conductivity reinforced by mixing graphite and silicon |
| CN103343266A (en) * | 2013-07-24 | 2013-10-09 | 上海交通大学 | High-thermal-conductivity graphite-high silicon aluminium-based composite material and preparation process for same |
| CN105734333A (en) * | 2016-03-10 | 2016-07-06 | 西北工业大学 | Heat conducting graphite/low-silicon/aluminium base composite and preparation method thereof |
| CN110016594A (en) * | 2019-05-07 | 2019-07-16 | 中铝广西崇左稀钪新材料科技有限公司 | A kind of die-casting rare earth aluminum alloy materials and preparation method thereof with high heat conductance |
| CN115161520A (en) * | 2022-06-07 | 2022-10-11 | 湖北新金洋资源股份公司 | High-strength and high-toughness heat-treatment-free casting aluminum alloy and preparation process thereof |
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