CN107723538B - Extra High Strength aluminium alloy and preparation method thereof - Google Patents
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- 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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- C22C21/00—Alloys based on aluminium
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- C22C21/10—Alloys based on aluminium with zinc as the next major constituent
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- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/18—Alloys based on aluminium with copper as the next major constituent with zinc
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- 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
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium as the next major constituent
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/053—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with zinc 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
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/057—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with copper as the next major constituent
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Abstract
The present invention provides a kind of Extra High Strength aluminium alloys, comprising: the Cu of 3.0wt%~10.0wt%；The Mg of 2.0wt%~9.7wt%；The Zn of 1.7wt%~38wt%；The Nd of 0.1wt%~1.3wt%；The Ni of 0.05wt%~2wt%；The Mn of 0.05wt%~1.77wt%；The Ti of 0.01wt%~0.5wt%；The Al of surplus.The present invention also provides a kind of preparation methods of Extra High Strength aluminium alloy.The present invention is to be specifically formulated, aluminum alloy materials are prepared using the technique of injection forming, microscopic structure obviously refines, and precipitated phase is tiny and is uniformly distributed, make its mechanical property almost without anisotropic, has the advantages that high intensity, high tenacity, high rigidity, light-weighted.The experimental results showed that Extra High Strength aluminium alloy provided by the invention is after T6 is handled, and tensile strength >=917MPa, yield strength >=874MPa.
Description
Technical field
The invention belongs to technical field of aluminum alloy technology more particularly to a kind of Extra High Strength aluminium alloy and preparation method thereof.
Background technique
Aluminium alloy has many advantages, such as that density is low, specific strength is high, good toughness and corrosion-resistant, is aerospace, communications and transportation, machine
Indispensable important feature material in tool manufacturing.It is strong to superelevation with the needs that national economy and national defense construction develop
Degree aluminum alloy materials propose great demand.
Prior art discloses a variety of high-strength aluminum alloy materials, for example, in seamless aluminium tubing national standard GB/T437.1-2000
Tensile strength and the maximum 7075T6 of yield strength are disclosed, tensile strength is up to 560MPa, and yield strength is up to
505MPa；Aluminium bar national standard GB/T3191-1998 discloses tensile strength and the maximum 7A07T6 of yield strength, and tensile strength is most
Greatly 530MPa, yield strength are up to 400MPa.It is resistance to that Chinese patent CN105838947B also discloses that a kind of superhigh intensity resists
Aluminum alloy materials are ground, after T6 is handled, tensile strength is up to 730MPa, and yield strength is up to 610MPa.But current aluminium
Alloy material tensile strength is unable to reach 800MPa.
Summary of the invention
In view of this, the present invention is public the purpose of the present invention is to provide a kind of Extra High Strength aluminium alloy and preparation method thereof
The Extra High Strength aluminum alloy materials opened have extra-high tensile strength and yield strength.
The present invention provides a kind of Extra High Strength aluminium alloys, comprising:
The Cu of 3.0wt%~10.0wt%；
The Mg of 2.0wt%~9.7wt%；
The Zn of 1.7wt%~38wt%；
The Nd of 0.1wt%~1.3wt%；
The Ni of 0.05wt%~2wt%；
The Mn of 0.05wt%~1.77wt%；
The Ti of 0.01wt%~0.5wt%；
The Al of surplus.
For above-mentioned aluminium alloy provided by the invention under each component interaction, the tension after T6 is handled with superelevation is strong
Degree and yield strength, tensile strength are more than 900MPa, and yield strength is more than 800MPa.
In one embodiment, the Extra High Strength aluminium alloy includes:
The Cu of 3.5wt%~9.5wt%；
The Mg of 2.5wt%~9.5wt%；
The Zn of 2wt%~35wt%；
The Nd of 0.2wt%~1.2wt%；
The Ni of 0.1wt%~1.8wt%；
The Mn of 0.1wt%~1.7wt%；
The Ti of 0.05wt%~0.45wt%；
The Al of surplus.
In one embodiment, the Extra High Strength aluminium alloy includes:
The Cu of 4.0wt%~9.0wt%；
The Mg of 3.0wt%~9.0wt%；
The Zn of 5wt%~30wt%；
The Nd of 0.3wt%~1.0wt%；
The Ni of 0.15wt%~1.5wt%；
The Mn of 0.15wt%~1.5wt%；
The Ti of 0.1wt%~0.4wt%；
The Al of surplus.
In one embodiment, the Extra High Strength aluminium alloy includes:
The Cu of 4.5wt%~8.5wt%；
The Mg of 3.5wt%~8.5wt%；
The Zn of 10wt%~25wt%；
The Nd of 0.5wt%~0.8wt%；
The Ni of 0.2wt%~1.2wt%；
The Mn of 0.2wt%~1.2wt%；
The Ti of 0.15wt%~0.35wt%；
The Al of surplus.
The present invention also provides the preparation methods of the Extra High Strength aluminium alloy described in above-mentioned technical proposal, including following step
It is rapid:
By Cu, Mg, Zn, Nd, Ni, Mn, Ti and Al melting, aluminum alloy melt is obtained；
The aluminum alloy melt is sprayed and is shaped, blank is obtained；
Deformation process and heat treatment are successively carried out to the blank.
The present invention obtains aluminum alloy melt directly by Cu, Mg, Zn, Nd, Ni, Mn, Ti and Al melting, and the present invention is to being used
Raw material have no it is specifically limited, can use each element simple substance, intermediate alloy can also be used.In one embodiment, it adopts
Raw material is to close among aluminium ingot, copper plate, magnesium ingot, zinc ingot metal, neodymium ingot, Al-Ni intermediate alloy, Al-Mn intermediate alloy and Al-Ti
Gold.
One canonical process of the melting are as follows:
Magnesium will be added after the fusing of aluminium ingot, Al-Ni intermediate alloy, Al-Mn intermediate alloy, Al-Ti intermediate alloy and copper plate
Refining agent is added after fusing in ingot and zinc ingot metal, and the fusing of neodymium ingot is added after upper dross is taken off to the greatest extent, obtains aluminum alloy melt after mixing evenly.
After being smelted into aluminum alloy melt, forming is sprayed, blank is obtained.In one embodiment, the present invention is preferably by institute
Stating aluminum alloy melt jet deposition is column or hollow shape or cuboid blank, sprays the specific process parameter of forming are as follows: protection gas
Body pressure is 0.1MPa~0.2MPa, and no fixed angle cyclic spray, injection pressure is 0.8MPa~1.5MPa, aluminum alloy melt temperature
Degree is 690 DEG C~870 DEG C, and spray distance is 400mm~900mm, and cooling disc spin speed is 15RPM~60RPM, under cooler pan
Reduction of speed degree is 3~15mm/s.
Injection forming successively carries out deformation process and heat treatment to it after obtaining blank, can be obtained the conjunction of superhigh intensity aluminium
Gold.In one embodiment of the invention, the deformation process specifically includes: the super-pressure conducting forging processing successively carried out and second
Secondary deformation process；Second of deformation process, which is selected from, to be squeezed, roll or forges and presses.
Specifically, injection forming uses forging press to carry out super-pressure conducting forging processing to it after obtaining blank, then carry out
It is crushed to profile, tubing or bar；Or it carries out that plate is made；Or it carries out forging and stamping and workpiece is made.The present invention is to institute
State super-pressure conducting forging processing, extruding, rolling or the technological parameter of forging and stamping without specifically limited, according to target alloy product into
Row selection.In a specific embodiment, the technological parameter of the super-pressure conducting forging processing are as follows: heating temperature be 420~
450℃；Forging and stamping pressure is 100MPa or more, and forge speed is 20mm/s or more.In one embodiment, the technique of the extruding
Parameter are as follows: 400~440 DEG C of heating temperature；10~30mm/s of extrusion speed.In one embodiment, the technique ginseng of the rolling
Number are as follows: 400~440 DEG C of heating temperature；5~35mm of reduction in pass；0.5~80m/min of mill speed.In one embodiment
In, the technological parameter of the forging and stamping are as follows: 400~440 DEG C of heating temperature；3~10mm/s of forge speed.
After deformation process, obtained blank is heat-treated, can be obtained ultrahigh-strength aluminum alloy.In a reality
It applies in example, the heat treatment is that T6 is heat-treated.Specifically, the heat treatment includes:
Ageing treatment is carried out after blank after deformation process is quenched.
In one embodiment, the temperature of the quenching is 440~465 DEG C, and soaking time is 40~80min；
In one embodiment, the temperature of the ageing treatment is 100~120 DEG C, and soaking time is 20~30h.
Aluminum alloy materials are prepared to be specifically formulated, using the technique of injection forming in the present invention, and microscopic structure is bright
Aobvious refinement, precipitated phase is tiny and is uniformly distributed, and is macroscopically controlled effectively so that the chemical component of material and group be made to be woven in.
Therefore, the mechanical property of material is almost without anisotropic, and material has high intensity, high tenacity, high rigidity, light-weighted excellent
Point has very good economic benefit and social benefit.Aluminium alloy provided by the invention be provided to Aeronautics and Astronautics, nobody
Machine and underwater vehicle etc. are needed using superhigh intensity, and light-weighted field is needed to apply again.
The experimental results showed that Extra High Strength aluminium alloy (code name 7Y79) provided by the invention is after T6 is handled, tension
Intensity >=917MPa, yield strength >=874MPa.
Specific embodiment
The technical scheme in the embodiments of the invention will be clearly and completely described below, it is clear that described implementation
Example is only a part of the embodiment of the present invention, instead of all the embodiments.Based on the embodiments of the present invention, this field is common
Technical staff's every other embodiment obtained without making creative work belongs to the model that the present invention protects
It encloses.
Examples 1 to 7, the Comparative Examples 1 to 5
Aluminum alloy materials are prepared according to formula shown in table 1:
The formula of 1 embodiment of the present invention of table and comparative example alloy product
| Ingredient (wt%) | Cu | Mg | Zn | Nd | Ni | Mn | Ti | Al | Shape of product |
| Embodiment 1 | 3.5 | 8.2 | 21 | 0.3 | 0.87 | 0.15 | 0.04 | Surplus | Stick |
| Embodiment 2 | 9.5 | 5.1 | 2.5 | 1.25 | 1.95 | 1.75 | 0.50 | Surplus | Stick |
| Embodiment 3 | 4.3 | 9.5 | 18 | 0.57 | 0.55 | 0.51 | 0.05 | Surplus | Stick |
| Embodiment 4 | 4.7 | 3.9 | 16 | 0.75 | 0.35 | 0.85 | 0.19 | Surplus | Stick |
| Embodiment 5 | 5.9 | 7.3 | 10 | 0.95 | 1.05 | 1.17 | 0.35 | Surplus | Pipe |
| Embodiment 6 | 6.8 | 2.5 | 31 | 0.21 | 0.10 | 0.32 | 0.08 | Surplus | Pipe |
| Embodiment 7 | 8.2 | 6.5 | 5 | 1.1 | 1.53 | 1.56 | 0.45 | Surplus | Pipe |
| Comparative example 1 | 1.8 | 2.5 | 5.8 | 0 | 0.08 | 0.03 | 0.02 | Surplus | Stick |
| Comparative example 2 | 3.5 | 2.2 | 5.5 | 0 | 0 | 0.01 | 0.02 | Surplus | Stick |
| Comparative example 3 | 15.3 | 2.3 | 6.1 | 0.05 | 0 | 0.01 | 0.01 | Surplus | Stick |
| Comparative example 4 | 5.1 | 18.2 | 7.7 | 0 | 2.5 | 0.01 | 0.03 | Surplus | Pipe |
| Comparative example 5 | 18.9 | 15.1 | 6.8 | 2.5 | 2.5 | 0.01 | 0.02 | Surplus | Pipe |
The preparation method is as follows:
According to component melting shown in table 1, with aluminium ingot, copper plate, magnesium ingot, zinc ingot metal, neodymium ingot, Al-Ni intermediate alloy, Al-
Mn intermediate alloy and Al-Ti intermediate alloy are raw material, first by aluminium ingot, Al-Ni intermediate alloy, Al-Mn intermediate alloy, Al-Ti
Magnesium ingot and zinc ingot metal is added after intermediate alloy and copper plate fusing, refining agent is added after fusing, neodymium ingot is added after upper dross is taken off to the greatest extent
Fusing, obtains aluminum alloy melt after mixing evenly；
Aluminum alloy melt injection is configured to column or hollow shape blank, sprays the technological parameter of forming are as follows:
Protective gas pressure is 0.15MPa, and no fixed angle cyclic spray, injection pressure is 1.2MPa, aluminum alloy melt temperature
Degree is 750 DEG C, spray distance 700mm, and cooling disc spin speed is 45RPM, and cooler pan decrease speed is 10mm/s；
Then super-pressure forging and extruding, the technological parameter of the super-pressure forging are as follows: mould are successively carried out to the blank
Having heating temperature is 420 DEG C, and blank heating temperature is 430 DEG C；Forging and stamping pressure is 120MPa, forge speed 20mm/s.It is described
The technological parameter of extruding are as follows: mould heating-up temperature is 400 DEG C, and blank heating temperature is 420 DEG C；Extrusion cylinder temperature is 420 DEG C, is squeezed
Pressure speed is 20mm/s.
Ageing treatment will be carried out after blank quenching after rolling, hardening heat is 450 DEG C, keeps the temperature water cooling after 1h；Timeliness temperature
Degree is 110 DEG C, and heat preservation for 24 hours, obtains ultrahigh-strength aluminum alloy stick or ultrahigh-strength aluminum alloy pipe.
The Extra High Strength aluminium alloy bars or Extra High Strength aluminium-alloy pipe are tested for the property, as a result referring to table 2, table 2
For the performance test results for the alloy product that the embodiment of the present invention and comparative example provide.
The performance test results for the alloy product that 2 embodiment of the present invention of table and comparative example provide
| Performance parameter | Tensile strength (MPa) | Yield strength (MPa) | Elongation percentage (%) |
| Embodiment 1 | 945 | 881 | 3.2 |
| Embodiment 2 | 930 | 870 | 4.2 |
| Embodiment 3 | 928 | 892 | 4.1 |
| Embodiment 4 | 832 | 786 | 4.5 |
| Embodiment 5 | 915 | 889 | 3.7 |
| Embodiment 6 | 957 | 895 | 2.9 |
| Embodiment 7 | 922 | 887 | 3.2 |
| Comparative example 1 | 575 | 522 | 8.5 |
| Comparative example 2 | 538 | 505 | 9.2 |
| Comparative example 3 | 565 | 519 | 9.9 |
| Comparative example 4 | 585 | 532 | 10.2 |
| Comparative example 5 | 571 | 509 | 10.6 |
In table 2, performance test methods are according to GB/T228.1-2010 " metal material stretching test first part: room temperature
Test method " carry out, testing equipment: U.S.'s Instelong test machine, model: 5585H.
The above is only a preferred embodiment of the present invention, it is noted that for the ordinary skill people of the art
For member, various improvements and modifications may be made without departing from the principle of the present invention, these improvements and modifications are also answered
It is considered as protection scope of the present invention.
Claims (8)
1. a kind of Extra High Strength aluminium alloy, comprising:
The Cu of 3.0wt% ~ 10.0wt%；
The Mg of 2.0wt% ~ 9.7wt%；
The Zn of 1.7wt% ~ 38wt%；
The Nd of 0.1wt% ~ 1.3wt%；
The Ni of 0.05wt% ~ 2wt%；
The Mn of 0.05wt% ~ 1.77wt%；
The Ti of 0.01wt% ~ 0.5wt%；
The Al of surplus；
Preparation method includes the following steps:
By Cu, Mg, Zn, Nd, Ni, Mn, Ti and Al melting, aluminum alloy melt is obtained；
The aluminum alloy melt is sprayed and is shaped, blank is obtained；
Deformation process and heat treatment are successively carried out to the blank.
2. Extra High Strength aluminium alloy according to claim 1 characterized by comprising
The Cu of 3.5wt% ~ 9.5wt%；
The Mg of 2.5wt% ~ 9.5wt%；
The Zn of 2wt% ~ 35wt%；
The Nd of 0.2wt% ~ 1.2wt%；
The Ni of 0.1wt% ~ 1.8wt%；
The Mn of 0.1wt% ~ 1.7wt%；
The Ti of 0.05wt% ~ 0.45wt%；
The Al of surplus.
3. Extra High Strength aluminium alloy according to claim 2 characterized by comprising
The Cu of 4.0wt% ~ 9.0wt%；
The Mg of 3.0wt% ~ 9.0wt%；
The Zn of 5wt% ~ 30wt%；
The Nd of 0.3wt% ~ 1.0wt%；
The Ni of 0.15wt% ~ 1.5wt%；
The Mn of 0.15wt% ~ 1.5wt%；
The Ti of 0.1wt% ~ 0.4wt%；
The Al of surplus.
4. Extra High Strength aluminium alloy according to claim 3 characterized by comprising
The Cu of 4.5wt% ~ 8.5wt%；
The Mg of 3.5wt% ~ 8.5wt%；
The Zn of 10wt% ~ 25wt%；
The Nd of 0.5wt% ~ 0.8wt%；
The Ni of 0.2wt% ~ 1.2wt%；
The Mn of 0.2wt% ~ 1.2wt%；
The Ti of 0.15wt% ~ 0.35wt%；
The Al of surplus.
5. the preparation method of Extra High Strength aluminium alloy described in claim 1, which comprises the following steps:
By Cu, Mg, Zn, Nd, Ni, Mn, Ti and Al melting, aluminum alloy melt is obtained；
The aluminum alloy melt is sprayed and is shaped, blank is obtained；
Deformation process and heat treatment are successively carried out to the blank.
6. preparation method according to claim 5, which is characterized in that the technological parameter of the injection forming are as follows:
Protective gas pressure is 0.1MPa ~ 0.2MPa, and no fixed angle cyclic spray, injection pressure is 0.8MPa ~ 1.5MPa, aluminium
Aluminium alloy temperature is 690 DEG C ~ 870 DEG C, and spray distance is 400mm ~ 900mm, and cooling disc spin speed is 15rpm ~ 60rpm,
Cooler pan decrease speed is 3 ~ 15mm/s.
7. preparation method according to claim 5, which is characterized in that the heat treatment includes:
Ageing treatment is carried out after blank after deformation process is quenched；
The temperature of the quenching is 440 ~ 465 DEG C, and soaking time is 40 ~ 80min；
The temperature of the ageing treatment is 100 ~ 120 DEG C, and soaking time is 20 ~ 30h.
8. preparation method according to claim 5, which is characterized in that the deformation process includes:
The super-pressure conducting forging processing and second of deformation process successively carried out；
Second of deformation process, which is selected from, to be squeezed, roll or forges and presses.
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