CN115652154B - High-strength heat-resistant high-scandium Al-Cu-Mg alloy and manufacturing process thereof - Google Patents
High-strength heat-resistant high-scandium Al-Cu-Mg alloy and manufacturing process thereof Download PDFInfo
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 118
- 239000000956 alloy Substances 0.000 title claims abstract description 118
- 229910052706 scandium Inorganic materials 0.000 title claims abstract description 49
- 229910017818 Cu—Mg Inorganic materials 0.000 title claims abstract description 40
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 22
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 33
- 238000000034 method Methods 0.000 claims abstract description 20
- 230000008569 process Effects 0.000 claims abstract description 16
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 15
- 229910052802 copper Inorganic materials 0.000 claims abstract description 9
- 238000010438 heat treatment Methods 0.000 claims description 45
- 238000007906 compression Methods 0.000 claims description 33
- 230000006835 compression Effects 0.000 claims description 33
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 31
- 239000011777 magnesium Substances 0.000 claims description 25
- 229910052749 magnesium Inorganic materials 0.000 claims description 23
- 239000006104 solid solution Substances 0.000 claims description 23
- 238000003723 Smelting Methods 0.000 claims description 22
- 230000032683 aging Effects 0.000 claims description 21
- SIXSYDAISGFNSX-UHFFFAOYSA-N scandium atom Chemical compound [Sc] SIXSYDAISGFNSX-UHFFFAOYSA-N 0.000 claims description 21
- 229910052761 rare earth metal Inorganic materials 0.000 claims description 17
- 239000010949 copper Substances 0.000 claims description 15
- 150000002910 rare earth metals Chemical class 0.000 claims description 15
- 229910000881 Cu alloy Inorganic materials 0.000 claims description 14
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims description 14
- WPPDFTBPZNZZRP-UHFFFAOYSA-N aluminum copper Chemical compound [Al].[Cu] WPPDFTBPZNZZRP-UHFFFAOYSA-N 0.000 claims description 14
- 238000001816 cooling Methods 0.000 claims description 14
- 238000010791 quenching Methods 0.000 claims description 14
- 230000000171 quenching effect Effects 0.000 claims description 14
- 238000000137 annealing Methods 0.000 claims description 12
- 239000012535 impurity Substances 0.000 claims description 9
- 229910052769 Ytterbium Inorganic materials 0.000 claims description 8
- 239000002994 raw material Substances 0.000 claims description 6
- 239000000463 material Substances 0.000 claims description 3
- 239000000243 solution Substances 0.000 claims description 2
- 238000000265 homogenisation Methods 0.000 abstract description 14
- 239000000470 constituent Substances 0.000 abstract description 12
- 239000011159 matrix material Substances 0.000 abstract description 8
- 229910000838 Al alloy Inorganic materials 0.000 abstract description 7
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- 210000001787 dendrite Anatomy 0.000 abstract description 2
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- 230000000052 comparative effect Effects 0.000 description 7
- 230000000694 effects Effects 0.000 description 6
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- 230000015572 biosynthetic process Effects 0.000 description 5
- 238000007872 degassing Methods 0.000 description 5
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- FAPWRFPIFSIZLT-UHFFFAOYSA-M Sodium chloride Chemical compound [Na+].[Cl-] FAPWRFPIFSIZLT-UHFFFAOYSA-M 0.000 description 2
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- 239000007787 solid Substances 0.000 description 2
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- 229910018182 Al—Cu Inorganic materials 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
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- VHHHONWQHHHLTI-UHFFFAOYSA-N hexachloroethane Chemical group ClC(Cl)(Cl)C(Cl)(Cl)Cl VHHHONWQHHHLTI-UHFFFAOYSA-N 0.000 description 1
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Abstract
The invention discloses a high-strength heat-resistant high-scandium Al-Cu-Mg alloy and a manufacturing process thereof, wherein the alloy comprises Cu, mg, mn, ti, zr, sc and Al as constituent elements. The invention overcomes the bottleneck problem of insufficient strength of the traditional heat-treatable reinforced aluminum alloy in a high-temperature service environment at 300-400 ℃ by implementing an effective and executable composite microalloying means and matching a reasonable thermomechanical treatment process system, and simultaneously adjusts different microstructures of parts requiring short-term or long-term service, thereby meeting the characteristics of high strength and heat resistance in a room temperature/high-temperature environment. Adopts a non-isothermal homogenization method at low temperature<Homogenizing at 350 ℃ to precipitate all Al as much as possible 3 (Sc，Zr)/Al 3 Sc. The Cu atoms are firstly diffused at the medium temperature (350-450 ℃), and dendrite segregation is eliminated as much as possible. The homogenization process is accelerated at a high temperature (450-520 ℃), so that the alloy components are uniform, and the interaction of Sc atoms and Cu atoms in an Al matrix is avoided to form a W phase in the high-temperature homogenization.
Description
Technical Field
The invention belongs to the technical field of aluminum alloy heat treatment, and particularly relates to a high-strength heat-resistant Sc-containing Al-Cu-Mg alloy and a manufacturing process thereof.
Background
As a typical representative of the aging-strengthening aluminum alloy, the 2 xxx-series (Al-Cu) alloy has high specific strength, excellent impact resistance, stress corrosion resistance and good weldability, and is widely applied to the fields of military, aerospace and the like. And is generally considered as a series of better heat resistance among aluminum alloys. Taking 2519 alloy as an example, the main alloying elements include Cu:5.3 to 6.4 percent of Mg:0.05 to 0.40 percent of Mn:0.10 to 0.50 percent of other elements such as Ti, zr, etc. However, in service environments exceeding 300 ℃, the strengthening compatibility in Al-Cu-Mg alloys is prone to coarsening, leading to rapid softening and failure of the alloy.
The classical thinking of heat resistance research of Al-Cu-Mg aging-strengthened alloy is to increase Cu/Mg ratio, the phase region in a phase diagram is alpha+theta, wherein the precipitated phase playing a main strengthening role is acicular theta ', theta' and a matrix are in semi-coherent relation, the strengthening effect of the alloy can be improved, and the alloy can bear large stress of more than 200MPa at the temperature of about 200 ℃ and has extremely excellent high-temperature resistance. However, for higher temperatures, such as 300-400 ℃ service environments, the theta' phase does not continue to maintain its excellent thermal stability but coarsens rapidly, resulting in rapid softening failure of the Al-Cu-Mg alloy also within the above interval.
Research shows that adding Sc into aluminum alloy precipitates Al in the solidification process 3 Sc serves as heterogeneous nuclear particles to play a role in refining grains, so that the mechanical property of the material is improved. Precipitation of dispersed Al coherent with the matrix during heat treatment 3 Sc particles have excellent thermal stability and are recognized as an effective means for improving the high-temperature service performance of aluminum-based alloys. However, because the price of Sc is too high, the solution thinking is to introduce independent Al outside the original precipitation sequence by adding rare earth elements such as Sc, zr and the like 3 X (x=sc, zr, etc.) is precipitated. The Zr element present in the Sc and the master alloy will form a group with Al 3 A Zr-rich shell similar to Sc particles encapsulates Sc Al 3 (Sc, zr) particles, core-shell structured Al 3 The mismatch degree of the (Sc, zr) and the alpha-Al matrix is lower, and the (Sc, zr) and the alpha-Al matrix have the functions of grain refinement and dispersion strengthening.
Although the addition of rare earth elements improves the mechanical properties, in Al-Cu-Mg alloys with higher Cu content, sc and Cu form a W phase, so that the content of Cu atoms in solid solution in the alloy is reduced, the density of a strengthening phase theta' in the alloy is further reduced, and the problem of mechanical property reduction is not effectively solved. Therefore, the invention provides a high scandium Al-Cu-Mg alloy heat treatment process, which reduces the formation of W phase and improves the mechanical property of the W phase in a severe service environment at 300-400 ℃.
Disclosure of Invention
The invention aims to overcome at least one defect of the prior art and provide a high-strength heat-resistant high-scandium Al-Cu-Mg alloy and a manufacturing process thereof.
The technical scheme adopted by the invention is as follows:
in a first aspect of the invention, there is provided:
a high-strength heat-resistant high-scandium Al-Cu-Mg alloy comprises the following components in mass percent: 5.3 to 6.4 percent of Cu, 0.05 to 0.40 percent of Mg, 0.10 to 0.50 percent of Mn, 0.02 to 0.10 percent of Ti, 0.10 to 0.25 percent of Zr, 0.20 to 0.40 percent of Yb, 0.30 to 0.80 percent of Sc, unavoidable impurities and the balance of Al.
In some examples of high strength, heat resistant, high scandium Al-Cu-Mg alloys, the content of Sc is 0.30 to 0.70%.
In some examples of high strength heat resistant high scandium Al-Cu-Mg alloys, the Sc content is 0.60%.
In some examples of high strength, heat resistant, high scandium Al-Cu-Mg alloys, the Yb content is 0.30%.
In some examples of high-strength heat-resistant high scandium Al-Cu-Mg alloys, yb: sc mass ratio = 2: (3-5).
In some examples of high-strength heat-resistant high scandium Al-Cu-Mg alloys, yb: sc mass ratio = 2:4.
in some examples of high strength, heat resistant, high scandium Al-Cu-Mg alloys, the content of Sc is 0.60% and the content of Yb is 0.30%.
In some examples of high strength heat resistant high scandium Al-Cu-Mg alloys, the unavoidable impurity content is not more than 0.1%.
The above definitions may be combined arbitrarily without conflict.
In a second aspect of the invention, there is provided:
the manufacturing process of the high-strength heat-resistant high-scandium Al-Cu-Mg alloy comprises the following steps of:
1) Smelting raw materials: preparing an aluminum ingot, a magnesium ingot, an aluminum intermediate alloy and a rare earth alloy, and smelting to obtain an alloy ingot;
2) And (3) annealing and compressing: carrying out non-isothermal homogenizing annealing on the alloy cast ingot prepared in the step 1), and carrying out multidirectional compression and quenching at the intermediate annealing temperature;
3) Solid solution aging: and (3) carrying out solid solution and double-stage aging treatment on the formed aluminum-copper alloy block, and taking out and air-cooling after the treatment is finished.
In some examples of manufacturing processes, the smelting temperature in step 1) is 720-760 ℃.
In some examples of manufacturing processes, the annealing compression operation in step 2) is as follows:
a) Homogenizing at 200-350 ℃, heating at a rate of 1-3 ℃/5-15 min, and performing one-pass compression at 300-350 ℃ with a deformation of 30-40%;
b) Homogenizing at 350-450 ℃, heating at a rate of 1-3 ℃/5-15 min, and performing one-pass compression on the deformed sample at 430-480 ℃ to obtain a deformation amount of 30-40%;
c) Homogenizing at 450-520 ℃, heating at a rate of 1-3 ℃/3-9 min, and compressing the deformed sample for one pass at 510-530 ℃ with a deformation amount of 30-40%.
In some examples of the manufacturing process, the solid solution treatment in the step 3) is to keep the temperature at 510-530 ℃ for 0.5-2 h.
In some examples of manufacturing processes, the two-stage aging treatment in step 3) is to first keep the temperature at 130-170 ℃ for 0.5-4 hours, and then keep the temperature at 170-220 ℃ for 0.5-48 hours.
In a third aspect of the invention, there is provided:
a section bar is prepared from the high-strength heat-resistant Al-Cu-Mg alloy in the first aspect of the invention or prepared from the high-strength heat-resistant Al-Cu-Mg alloy prepared by the manufacturing process in the second aspect of the invention.
The invention has the beneficial effects that:
the invention overcomes the bottleneck problem of insufficient strength of the traditional heat-treatable reinforced aluminum alloy in a high-temperature service environment at 300-400 ℃ by implementing an effective and executable composite microalloying means and matching a reasonable thermomechanical treatment process system, and simultaneously adjusts different microstructures of parts requiring short-term or long-term service, thereby meeting the characteristics of high strength and heat resistance in a room temperature/high-temperature environment.
The invention provides a preparation method for controlling the formation of a W phase in a high scandium Al-Cu-Mg alloy from the non-isothermal homogenization deformation heat treatment process angle for the first time to obtain the high-strength heat-resistant aluminum alloy. The method adopts a non-isothermal homogenization method at low temperature<Homogenizing at 350 ℃ to precipitate all Al as much as possible 3 (Sc，Zr)/Al 3 Sc. The Cu atoms are firstly diffused at the medium temperature (350-450 ℃), and dendrite segregation is eliminated as much as possible. High temperature (450-520 ℃) accelerationAnd in the homogenization process, the alloy components are uniform, and the interaction of Sc atoms and Cu atoms in the Al matrix is avoided to form a W phase in the high-temperature homogenization. In addition, the interaction strength of Yb, zr and Sc elements in the low-temperature homogenization process is very low, which indicates that the rare earth Yb can promote the solid solution of the Zr and Sc elements, improve the solid solubility of the Zr and Sc in an aluminum matrix, and the low-temperature homogenization process is characterized in that the alloy comprises Al 3 (Sc,Zr)/Al 3 The amount of Sc precipitated increases. Meanwhile, the addition of Yb element prevents the formation of W phase in the high temperature process, so that the W phase is further reduced.
The invention can separate out enough GP zone and dislocation effect after low temperature short time aging (150 ℃ for 30min-4 h), and the deformation strengthening effect is reserved, and simultaneously, the tiny dispersed GP zone and dislocation provide a large number of nucleation points for theta' phase, thereby improving the alloy strength.
Drawings
FIG. 1 is a microstructure of the high scandium Al-Cu-Mg alloy produced in example 4.
Detailed Description
In a first aspect of the invention, there is provided:
a high-strength heat-resistant high-scandium Al-Cu-Mg alloy comprises the following components in mass percent: 5.3 to 6.4 percent of Cu, 0.05 to 0.40 percent of Mg, 0.10 to 0.50 percent of Mn, 0.02 to 0.10 percent of Ti, 0.10 to 0.25 percent of Zr, 0.20 to 0.40 percent of Yb, 0.30 to 0.80 percent of Sc, unavoidable impurities and the balance of Al.
In some examples of high strength heat resistant high scandium Al-Cu-Mg alloys, the mass composition is: 5.56 to 6.35 percent of Cu, 0.25 to 0.36 percent of Mg, 0.24 to 0.47 percent of Mn, 0.06 to 0.10 percent of Ti, 0.10 to 0.17 percent of Zr, 0.20 to 0.40 percent of Yb, 0.30 to 0.80 percent of Sc, unavoidable impurities and the balance of Al.
Yb can promote solid solution of Zr and Sc elements, improve solid solubility of Zr and Sc in an aluminum matrix, and realize Al in the low-temperature homogenization process 3 (Sc,Zr)/Al 3 The amount of Sc precipitated increases. Meanwhile, the addition of Yb element prevents the formation of W phase in the high temperature process, so that the W phase is further reduced.
In some examples of high strength, heat resistant, high scandium Al-Cu-Mg alloys, the content of Sc is 0.30 to 0.70%.
In some examples of high strength, heat resistant, high scandium Al-Cu-Mg alloys, the Yb content is 0.30%.
In some examples of high-strength heat-resistant high scandium Al-Cu-Mg alloys, yb: sc mass ratio = 2: (3-5).
In some examples of high-strength heat-resistant high scandium Al-Cu-Mg alloys, yb: sc mass ratio = 2:4.
in some examples of high strength, heat resistant, high scandium Al-Cu-Mg alloys, the content of Sc is 0.60% and the content of Yb is 0.30%. The data show that at this level, tensile strength at room temperature and 300 ℃ can be maximized while elongation is minimized.
Impurities have a detrimental effect on the properties of the product, and in order to better stabilize the quality of the product, in some examples of high-strength heat-resistant high scandium Al-Cu-Mg alloys, the unavoidable impurity content is not more than 0.1%.
In a second aspect of the invention, there is provided:
the manufacturing process of the high-strength heat-resistant high-scandium Al-Cu-Mg alloy comprises the following steps of:
1) Smelting raw materials: preparing an aluminum ingot, a magnesium ingot, an aluminum intermediate alloy and a rare earth alloy, and smelting to obtain an alloy ingot;
2) And (3) annealing and compressing: carrying out non-isothermal homogenizing annealing on the alloy cast ingot prepared in the step 1), and carrying out multidirectional compression and quenching at the intermediate annealing temperature;
3) Solid solution aging: and (3) carrying out solid solution and double-stage aging treatment on the formed aluminum-copper alloy block, and taking out and air-cooling after the treatment is finished.
In some examples of manufacturing processes, the smelting temperature in step 1) is 720-760 ℃. The raw materials can be fully and evenly melted and mixed at the temperature.
In some examples of manufacturing processes, the annealing compression operation in step 2) is as follows:
a) Homogenizing at 200-350 ℃, heating at a rate of 1-3 ℃/5-15 min, and performing one-pass compression at 300-350 ℃ with a deformation of 30-40%;
b) Homogenizing at 350-450 ℃, heating at a rate of 1-3 ℃/5-15 min, and performing one-pass compression on the deformed sample at 430-480 ℃ to obtain a deformation amount of 30-40%;
c) Homogenizing at 450-520 ℃, heating at a rate of 1-3 ℃/3-9 min, and compressing the deformed sample for one pass at 510-530 ℃ with a deformation amount of 30-40%.
Experimental data show that under the condition, the high-quality high-strength heat-resistant high scandium Al-Cu-Mg alloy can be further obtained.
In some examples of the manufacturing process, the solid solution treatment in the step 3) is to keep the temperature at 510-530 ℃ for 0.5-2 h.
In some examples of manufacturing processes, the two-stage aging treatment in step 3) is to first keep the temperature at 130-170 ℃ for 0.5-4 hours, and then keep the temperature at 170-220 ℃ for 0.5-48 hours.
In a third aspect of the invention, there is provided:
a section bar is prepared from the high-strength heat-resistant Al-Cu-Mg alloy in the first aspect of the invention or prepared from the high-strength heat-resistant Al-Cu-Mg alloy prepared by the manufacturing process in the second aspect of the invention.
The present invention will be described in detail with reference to examples, comparative examples and experimental data.
In each embodiment, the alloy comprises the following chemical components, by weight, 5.3-6.4% of Cu, 0.05-0.40% of Mg, 0.10-0.50% of Mn, 0.02-0.10% of Ti, 0.10-0.25% of Zr, 0.20-0.40% of Yb and 0.30-0.80% of Sc. Pure Al and Mg cast ingots, al-50Cu, al-10Mn, al-4Ti, al-3Sc, al-5Zr and Al-10Yb intermediate alloys are selected as raw materials.
The multi-element refining agent and the degassing agent are general in the field (the mass ratio of the refining agent to the smelting ingredients is (1-3): 100), the multi-element composite refining agent comprises 20wt% of NaCl, 20wt% of KCl, 35wt% of NaF and 25wt% of LiF, and the mass ratio of the degassing agent to the smelting ingredients is 1:100, wherein the degassing agent is hexachloroethane. When the purity of the raw material is high, a multi-element refining agent and a degassing agent may not be added. The multi-element refining agent and the degassing agent have no influence on the performance of the alloy.
The technical scheme of the invention is further described below by combining examples. In order to obtain a product with more stable quality, the impurity in each example is controlled below 0.1%.
Example 1
1) According to the weight percentage of the constituent elements, cu 5.71%, mg 0.32%, mn 0.24%, ti 0.09%, zr 0.12%, yb 0.30%, sc 0.30% and the balance Al are taken; preparing an aluminum ingot, a magnesium ingot, an aluminum intermediate alloy and a rare earth alloy, and smelting at 720-760 ℃ to obtain an alloy ingot;
2) Homogenizing the prepared alloy cast ingot at 200-350 ℃, heating at a rate of 1 ℃/15min, and performing one-pass compression at 350 ℃ to obtain a deformation of 40%; homogenizing at 350-450 ℃, heating at a rate of 1 ℃/8min, rotating the deformed sample at 450 ℃ for 90 ℃ twice, and then performing one-pass compression, wherein the deformation is 40%; homogenizing at 450-520 ℃, heating at a rate of 1 ℃/3min, rotating the deformed sample twice at 520 ℃ by 90 degrees, then compressing for one pass, wherein the deformation amount is 40%, and quenching;
3) And (3) carrying out solid solution (heat preservation at 520 ℃ for 1 h) +double-stage aging treatment (150 ℃ for 30min-4h,200 ℃ for 30min-48 h) on the formed aluminum-copper alloy block, taking out a sample, and then carrying out air cooling.
Example 2
1) According to the weight percentage of the constituent elements, cu 5.62%, mg 0.29%, mn 0.28%, ti 0.10%, zr 0.16%, yb 0.30%, sc 0.40% and the balance Al are taken; preparing an aluminum ingot, a magnesium ingot, an aluminum intermediate alloy and a rare earth alloy, and smelting at 720-760 ℃ to obtain an alloy ingot;
2) Homogenizing the prepared alloy cast ingot at 200-350 ℃, heating at a rate of 1 ℃/15min, and performing one-pass compression at 350 ℃ to obtain a deformation of 40%; homogenizing at 350-450 ℃, heating at a rate of 1 ℃/8min, rotating the deformed sample at 450 ℃ for 90 ℃ twice, and then performing one-pass compression, wherein the deformation is 40%; homogenizing at 450-520 ℃, heating at a rate of 1 ℃/3min, rotating the deformed sample twice at 520 ℃ by 90 degrees, then compressing for one pass, wherein the deformation amount is 40%, and quenching;
3) And (3) carrying out solid solution (heat preservation at 520 ℃ for 1 h) +double-stage aging treatment (150 ℃ for 30min-4h,200 ℃ for 30min-48 h) on the formed aluminum-copper alloy block, taking out a sample, and then carrying out air cooling.
Example 3
1) According to the weight percentage of the constituent elements, cu 5.56%, mg 0.34%, mn 0.34%, ti 0.08%, zr 0.11%, yb 0.30%, sc 0.50% and the balance Al are taken; preparing an aluminum ingot, a magnesium ingot, an aluminum intermediate alloy and a rare earth alloy, and smelting at 720-760 ℃ to obtain an alloy ingot;
2) Homogenizing the prepared alloy cast ingot at 200-350 ℃, heating at a rate of 1 ℃/15min, and performing one-pass compression at 350 ℃ to obtain a deformation of 40%; homogenizing at 350-450 ℃, heating at a rate of 1 ℃/8min, rotating the deformed sample at 450 ℃ for 90 ℃ twice, and then performing one-pass compression, wherein the deformation is 40%; homogenizing at 450-520 ℃, heating at a rate of 1 ℃/3min, rotating the deformed sample twice at 520 ℃ by 90 degrees, then compressing for one pass, wherein the deformation amount is 40%, and quenching;
3) And (3) carrying out solid solution (heat preservation at 520 ℃ for 1 h) +double-stage aging treatment (150 ℃ for 30min-4h,200 ℃ for 30min-48 h) on the formed aluminum-copper alloy block, taking out a sample, and then carrying out air cooling.
Example 4
1) According to the weight percentage of the constituent elements, cu 5.84%, mg 0.25%, mn 0.41%, ti 0.06%, zr 0.12%, yb 0.30%, sc 0.60% and the balance Al are taken; preparing an aluminum ingot, a magnesium ingot, an aluminum intermediate alloy and a rare earth alloy, and smelting at 720-760 ℃ to obtain an alloy ingot;
2) Homogenizing the prepared alloy cast ingot at 200-350 ℃, heating at a rate of 1 ℃/15min, and performing one-pass compression at 350 ℃ to obtain a deformation of 40%; homogenizing at 350-450 ℃, heating at a rate of 1 ℃/8min, rotating the deformed sample at 450 ℃ for 90 ℃ twice, and then performing one-pass compression, wherein the deformation is 40%; homogenizing at 450-520 ℃, heating at a rate of 1 ℃/3min, rotating the deformed sample twice at 520 ℃ by 90 degrees, then compressing for one pass, wherein the deformation amount is 40%, and quenching;
3) And (3) carrying out solid solution (heat preservation at 520 ℃ for 1 h) +double-stage aging treatment (150 ℃ for 30min-4h,200 ℃ for 30min-48 h) on the formed aluminum-copper alloy block, taking out a sample, and then carrying out air cooling.
Example 5
1) According to the weight percentage of the constituent elements, cu 5.92%, mg 0.31%, mn 0.36%, ti 0.09%, zr 0.15%, yb 0.30%, sc 0.70% and the balance Al are taken; preparing an aluminum ingot, a magnesium ingot, an aluminum intermediate alloy and a rare earth alloy, and smelting at 720-760 ℃ to obtain an alloy ingot;
2) Homogenizing the prepared alloy cast ingot at 200-350 ℃, heating at a rate of 1 ℃/15min, and performing one-pass compression at 350 ℃ to obtain a deformation of 40%; homogenizing at 350-450 ℃, heating at a rate of 1 ℃/8min, rotating the deformed sample at 450 ℃ for 90 ℃ twice, and then performing one-pass compression, wherein the deformation is 40%; homogenizing at 450-520 ℃, heating at a rate of 1 ℃/3min, rotating the deformed sample twice at 520 ℃ by 90 degrees, then compressing for one pass, wherein the deformation amount is 40%, and quenching;
3) And (3) carrying out solid solution (heat preservation at 520 ℃ for 1 h) +double-stage aging treatment (150 ℃ for 30min-4h,200 ℃ for 30min-48 h) on the formed aluminum-copper alloy block, taking out a sample, and then carrying out air cooling.
Example 6
1) According to the weight percentage of the constituent elements, 6.01 percent of Cu, 0.28 percent of Mg, 0.29 percent of Mn, 0.10 percent of Ti, 0.17 percent of Zr, 0.30 percent of Yb, 0.80 percent of Sc and the balance of Al are taken; preparing an aluminum ingot, a magnesium ingot, an aluminum intermediate alloy and a rare earth alloy, and smelting at 720-760 ℃ to obtain an alloy ingot;
2) Homogenizing the prepared alloy cast ingot at 200-350 ℃, heating at a rate of 1 ℃/15min, and performing one-pass compression at 350 ℃ to obtain a deformation of 40%; homogenizing at 350-450 ℃, heating at a rate of 1 ℃/8min, rotating the deformed sample at 450 ℃ for 90 ℃ twice, and then performing one-pass compression, wherein the deformation is 40%; homogenizing at 450-520 ℃, heating at a rate of 1 ℃/3min, rotating the deformed sample twice at 520 ℃ by 90 degrees, then compressing for one pass, wherein the deformation amount is 40%, and quenching;
3) And (3) carrying out solid solution (heat preservation at 520 ℃ for 1 h) +double-stage aging treatment (150 ℃ for 30min-4h,200 ℃ for 30min-48 h) on the formed aluminum-copper alloy block, taking out a sample, and then carrying out air cooling.
Example 7
1) According to the weight percentage of the constituent elements, 6.13t percent of Cu, 0.34 percent of Mg, 0.45 percent of Mn, 0.07 percent of Ti, 0.12 percent of Zr, 0.20 percent of Yb, 0.60 percent of Sc and the balance of Al are taken; preparing an aluminum ingot, a magnesium ingot, an aluminum intermediate alloy and a rare earth alloy, and smelting at 720-760 ℃ to obtain an alloy ingot;
2) Homogenizing the prepared alloy cast ingot at 200-350 ℃, heating at a rate of 1 ℃/15min, and performing one-pass compression at 350 ℃ to obtain a deformation of 40%; homogenizing at 350-450 ℃, heating at a rate of 1 ℃/8min, rotating the deformed sample at 450 ℃ for 90 ℃ twice, and then performing one-pass compression, wherein the deformation is 40%; homogenizing at 450-520 ℃, heating at a rate of 1 ℃/3min, rotating the deformed sample twice at 520 ℃ by 90 degrees, then compressing for one pass, wherein the deformation amount is 40%, and quenching;
3) And (3) carrying out solid solution (heat preservation at 520 ℃ for 1 h) +double-stage aging treatment (150 ℃ for 30min-4h,200 ℃ for 30min-48 h) on the formed aluminum-copper alloy block, taking out a sample, and then carrying out air cooling.
Example 8
1) According to the weight percentage of the constituent elements, 6.35 percent of Cu, 0.36 percent of Mg, 0.47 percent of Mn, 0.08 percent of Ti, 0.1 percent of Zr, 0.40 percent of Yb, 0.60 percent of Sc and the balance of Al are taken; preparing an aluminum ingot, a magnesium ingot, an aluminum intermediate alloy and a rare earth alloy, and smelting at 720-760 ℃ to obtain an alloy ingot;
2) Homogenizing the prepared alloy cast ingot at 200-350 ℃, heating at a rate of 1 ℃/15min, and performing one-pass compression at 350 ℃ to obtain a deformation of 40%; homogenizing at 350-450 ℃, heating at a rate of 1 ℃/8min, rotating the deformed sample at 450 ℃ for 90 ℃ twice, and then performing one-pass compression, wherein the deformation is 40%; homogenizing at 450-520 ℃, heating at a rate of 1 ℃/3min, rotating the deformed sample twice at 520 ℃ by 90 degrees, then compressing for one pass, wherein the deformation amount is 40%, and quenching;
3) And (3) carrying out solid solution (heat preservation at 520 ℃ for 1 h) +double-stage aging treatment (150 ℃ for 30min-4h,200 ℃ for 30min-48 h) on the formed aluminum-copper alloy block, taking out a sample, and then carrying out air cooling.
Example 9
1) According to the weight percentage of the constituent elements, cu 5.84%, mg 0.25%, mn 0.41%, ti 0.06%, zr 0.12%, yb 0.30%, sc 0.60% and the balance Al are taken; preparing an aluminum ingot, a magnesium ingot, an aluminum intermediate alloy and a rare earth alloy, and smelting at 720-760 ℃ to obtain an alloy ingot;
2) Homogenizing the prepared alloy ingot at 450 ℃, heating at a rate of 1 ℃/10min, and performing one-pass compression at 450 ℃ to obtain a deformation amount of 40%; homogenizing at 520 ℃, heating at a rate of 1 ℃/2min, rotating the deformed sample twice at 520 ℃ by 90 degrees, then compressing for one pass, wherein the deformation amount is 40%, and quenching;
3) And (3) carrying out solid solution (heat preservation at 520 ℃ for 1 h) +double-stage aging treatment (150 ℃ for 30min-4h,200 ℃ for 30min-48 h) on the formed aluminum-copper alloy block, taking out a sample, and then carrying out air cooling.
Comparative example 1
1) According to the weight percentage of the constituent elements, cu 5.84%, mg 0.25%, mn 0.41%, ti 0.06%, zr 0.12%, yb 0.30%, sc 0.10% and the balance Al are taken; preparing an aluminum ingot, a magnesium ingot, an aluminum intermediate alloy and a rare earth alloy, and smelting at 720-760 ℃ to obtain an alloy ingot;
2) Homogenizing the prepared alloy cast ingot at 200-350 ℃, heating at a rate of 1 ℃/15min, and performing one-pass compression at 350 ℃ to obtain a deformation of 40%; homogenizing at 350-450 ℃, heating at a rate of 1 ℃/8min, rotating the deformed sample at 450 ℃ for 90 ℃ twice, and then performing one-pass compression, wherein the deformation is 40%; homogenizing at 450-520 ℃, heating at a rate of 1 ℃/3min, rotating the deformed sample twice at 520 ℃ by 90 degrees, then compressing for one pass, wherein the deformation amount is 40%, and quenching;
3) And (3) carrying out solid solution (heat preservation at 520 ℃ for 1 h) +double-stage aging treatment (150 ℃ for 30min-4h,200 ℃ for 30min-48 h) on the formed aluminum-copper alloy block, taking out a sample, and then carrying out air cooling.
Comparative example 2
1) According to the weight percentage of the constituent elements, cu 5.84%, mg 0.25%, mn 0.41%, ti 0.06%, zr 0.12%, yb 0.30%, sc 1.0% and the balance Al are taken; preparing an aluminum ingot, a magnesium ingot, an aluminum intermediate alloy and a rare earth alloy, and smelting at 720-760 ℃ to obtain an alloy ingot;
2) Homogenizing the prepared alloy cast ingot at 200-350 ℃, heating at a rate of 1 ℃/15min, and performing one-pass compression at 350 ℃ to obtain a deformation of 40%; homogenizing at 350-450 ℃, heating at a rate of 1 ℃/8min, rotating the deformed sample at 450 ℃ for 90 ℃ twice, and then performing one-pass compression, wherein the deformation is 40%; homogenizing at 450-520 ℃, heating at a rate of 1 ℃/3min, rotating the deformed sample twice at 520 ℃ by 90 degrees, then compressing for one pass, wherein the deformation amount is 40%, and quenching;
3) And (3) carrying out solid solution (heat preservation at 520 ℃ for 1 h) +double-stage aging treatment (150 ℃ for 30min-4h,200 ℃ for 30min-48 h) on the formed aluminum-copper alloy block, taking out a sample, and then carrying out air cooling.
Comparison of the Performance of Al-Cu-Mg alloys with different Sc content
Mechanical property tests (room temperature and 300 ℃) were carried out on the high scandium Al-Cu-Mg alloy plates obtained in the examples and the comparative examples, respectively, wherein the melting point of the alloy was measured using a Differential Scanning Calorimeter (DSC); the strength and elongation test method is according to GB/T228.1-2010 section 1 of tensile test of metallic Material: room temperature test method. The results are shown in Table 1.
TABLE 1
1) Comparative examples 1 to 6 show that the strength of the alloy is improved and reduced with increasing amount of Sc;
2) The homogenization temperature of example 9 was higher than Al 3 (Sc, zr) optimal precipitation temperature, generating more W phase, resulting in a significant decrease in the performance of the alloy;
3) The Sc content of comparative example 1 and comparative example 2 is not within a limited range, and the mechanical properties of the alloy are significantly reduced.
FIG. 1 is a microstructure of a high scandium Al-Cu-Mg alloy prepared in example 4, from which it can be seen that the second phase is significantly reduced, the redissolution effect is significant, and a large amount of L1 is precipitated during homogenization 2 -Al 3 The (Sc, zr) particles achieve the effects of solid solution strengthening and precipitation strengthening, thereby improving the room temperature and high temperature performance of the alloy. In addition, the homogenization temperature is increased, and the Sc atom diffusion rate is accelerated to generate more W phase. However, the addition of elemental Yb can hinder the formation of the W phase of the homogenization process and determine Yb: sc is 1:2 with best effect.
The foregoing description of the preferred embodiments of the invention is not intended to be limiting, but rather is intended to cover all modifications, equivalents, alternatives, and improvements that fall within the spirit and scope of the invention.
Claims (8)
1. A manufacturing process of a high-strength heat-resistant high-scandium Al-Cu-Mg alloy comprises the following components in parts by mass: 5.3 to 6.4 percent of Cu, 0.05 to 0.40 percent of Mg, 0.10 to 0.50 percent of Mn, 0.02 to 0.10 percent of Ti, 0.10 to 0.25 percent of Zr, 0.20 to 0.40 percent of Yb, 0.30 to 0.80 percent of Sc, unavoidable impurities and the balance of Al, and the method comprises the following steps:
1) Smelting raw materials: preparing an aluminum ingot, a magnesium ingot, an aluminum intermediate alloy and a rare earth alloy, and smelting to obtain an alloy ingot;
2) And (3) annealing and compressing: carrying out non-isothermal homogenizing annealing on the alloy cast ingot prepared in the step 1), and carrying out multidirectional compression and quenching at the intermediate annealing temperature; the annealing compression operation is as follows:
homogenizing at 200-350 ℃, heating at a rate of 1-3 ℃/5-15 min, and performing one-pass compression at 300-350 ℃ with a deformation of 30-40%;
homogenizing at 350-450 ℃, heating at a rate of 1-3 ℃/5-15 min, and performing one-pass compression on the deformed sample at 430-480 ℃ to obtain a deformation amount of 30-40%;
homogenizing at 450-520 ℃, heating at a rate of 1-3 ℃/3-9 min, and compressing the deformed sample for one pass at 510-530 ℃ with a deformation amount of 30-40%;
3) Solid solution aging: and (3) carrying out solid solution and double-stage aging treatment on the formed aluminum-copper alloy block, and taking out and air-cooling after the treatment is finished.
2. The process according to claim 1, wherein the content of Sc is 0.30 to 0.70%.
3. The manufacturing process according to claim 2, characterized in that Yb: sc mass ratio = 2: (3-5).
4. A manufacturing process according to any one of claims 1 to 3, wherein the unavoidable impurity content is not more than 0.1%.
5. The manufacturing process according to claim 1, wherein the smelting temperature in step 1) is 720-760 ℃.
6. The process according to claim 1 or 5, wherein the solution treatment in step 3) is carried out at 510-530 ℃ for 0.5-2 hours.
7. The process according to claim 1 or 5, wherein the two-stage aging treatment in step 3) is performed by first maintaining the temperature at 130-170 ℃ for 0.5-4 hours and then maintaining the temperature at 170-220 ℃ for 0.5-48 hours.
8. A profile material, characterized in that the profile material is prepared from the high-strength heat-resistant high scandium Al-Cu-Mg alloy prepared by the manufacturing process according to any one of claims 1 to 7.
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