CN117778913A - High-strength corrosion-resistant aluminum alloy super-thick forging and preparation method and application thereof - Google Patents
High-strength corrosion-resistant aluminum alloy super-thick forging and preparation method and application thereof Download PDFInfo
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- 238000005242 forging Methods 0.000 title claims abstract description 122
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 102
- 230000007797 corrosion Effects 0.000 title claims abstract description 64
- 238000005260 corrosion Methods 0.000 title claims abstract description 64
- 238000002360 preparation method Methods 0.000 title claims abstract description 11
- 238000000034 method Methods 0.000 claims abstract description 26
- 238000005336 cracking Methods 0.000 claims abstract description 4
- 230000032683 aging Effects 0.000 claims description 72
- 238000010438 heat treatment Methods 0.000 claims description 45
- 230000035882 stress Effects 0.000 claims description 42
- 230000009467 reduction Effects 0.000 claims description 29
- 238000001816 cooling Methods 0.000 claims description 25
- 238000004321 preservation Methods 0.000 claims description 25
- 238000010791 quenching Methods 0.000 claims description 14
- 230000000171 quenching effect Effects 0.000 claims description 14
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 11
- 238000004519 manufacturing process Methods 0.000 claims description 7
- 230000000630 rising effect Effects 0.000 claims description 6
- 229910045601 alloy Inorganic materials 0.000 abstract description 30
- 239000000956 alloy Substances 0.000 abstract description 30
- 230000008569 process Effects 0.000 abstract description 14
- 238000001556 precipitation Methods 0.000 abstract description 8
- 239000013078 crystal Substances 0.000 abstract description 7
- 239000002344 surface layer Substances 0.000 abstract description 7
- 239000011159 matrix material Substances 0.000 abstract description 5
- 229910052742 iron Inorganic materials 0.000 abstract description 4
- 229910052748 manganese Inorganic materials 0.000 abstract description 4
- 238000009827 uniform distribution Methods 0.000 abstract description 3
- 239000000243 solution Substances 0.000 description 30
- 229910018569 Al—Zn—Mg—Cu Inorganic materials 0.000 description 15
- 238000005096 rolling process Methods 0.000 description 15
- 230000000052 comparative effect Effects 0.000 description 14
- 238000012360 testing method Methods 0.000 description 9
- 238000005266 casting Methods 0.000 description 8
- 230000001276 controlling effect Effects 0.000 description 7
- 238000005520 cutting process Methods 0.000 description 7
- 229910052691 Erbium Inorganic materials 0.000 description 4
- 229910052725 zinc Inorganic materials 0.000 description 4
- 229910052802 copper Inorganic materials 0.000 description 3
- 229910052706 scandium Inorganic materials 0.000 description 3
- 229910017706 MgZn Inorganic materials 0.000 description 2
- 229910017708 MgZn2 Inorganic materials 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 2
- 238000013461 design Methods 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910000510 noble metal Inorganic materials 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
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Abstract
The invention discloses a high-strength corrosion-resistant aluminum alloy super-thick forging and a preparation method and application thereof, which not only ensure that the alloy has higher strength, but also increase the Cu element content in a grain boundary precipitation phase, reduce the potential difference between the grain boundary phase and a matrix, inhibit the corrosion of primary cells at the grain boundary and improve the stress corrosion resistance of the alloy by reasonably adjusting the content and the proportion of main alloy elements. By controlling the content and the proportion of Fe and Mn elements, the content of indissolvable coarse phases in the alloy is reduced, corrosion cracking caused by indissolvable coarse phases is reduced, and the stress corrosion resistance is improved. The forging process of upsetting and thickness extension of the cast ingot is adopted, and the parameters such as the extension depression amount, the extension feed amount, the depression speed and the like are innovatively distributed, so that the strain is transmitted from the core part of the cast ingot to the surface layer of the cast ingot, and the uniform distribution is realized in the thickness direction of the cast ingot, so that the surface layer of the ultra-thick forging has the same crystal grain structure and uniform mechanical property as the core part of the plate.
Description
Technical Field
The invention belongs to the technical field of aluminum alloy, and particularly relates to a high-strength corrosion-resistant aluminum alloy super-thick forging, a preparation method and application thereof.
Background
The Al-Zn-Mg-Cu alloy is very suitable for aerospace equipment due to high specific strength, low density and good formability. A common problem with Al-Zn-Mg-Cu high strength aluminum alloys is the contradiction between strength and stress corrosion properties. The occurrence of stress corrosion fracture is not obvious, and the hazard is extremely high, so that the popularization and the application of the high-strength aluminum alloy are severely restricted.
The large-size aluminum alloy plate is a raw material for manufacturing large parts in the aerospace field, and with the development of integrated design of parts, the requirements on the large-size plate are increased more and more, and the performance requirements are also increased more and more. The large plate is usually prepared by adopting an ingot rolling mode, but for plates with larger thickness, the existing ingot rolling mode cannot introduce enough strain quantity in the thickness center of the plate due to the limitation of ingot thickness and equipment capacity, so that the uniformity of the grain structure of the plate is poor. Poor uniformity of the grain structure of the plate directly influences the uniformity of mechanical property and stress corrosion property, and the service life of the plate is seriously influenced.
At present, related patent reports about a method for improving stress corrosion performance of an Al-Zn-Mg-Cu alloy and a method for preparing a forging piece are available. For example, patent CN115710661A discloses an Al-Zn-Mg-Cu aluminum alloy and a method for improving stress corrosion performance thereof, wherein the aluminum alloy comprises, by weight, 7.0-10.0% of Zn, 1.0-1.8% of Mg, 1.0-2.3% of Cu, 0.08-0.12% of Zr, 0.02-0.06% of Ti, less than or equal to 0.08% of Fe, less than or equal to 0.06% of Si, less than or equal to 0.05% of Mn, less than or equal to 0.05% of Cr, sc and Er, the content of Sc and Er is less than or equal to 0.5 and less than or equal to 1.0% of Sc/Er, and the balance is Al. According to the patent, precipitation of MgZn2 phases in crystals is promoted by adding Sc and Er, and the number of MgZn2 phases in crystal boundaries is reduced, so that the stress corrosion performance is improved, but the alloy is not beneficial to low-cost manufacture and application of aluminum alloy due to the addition of Sc and Er elements with high price. Patent CN111974919a discloses a forging method for improving anisotropy of a 7XXX aluminum alloy forging, which adopts a forging process mode of high-temperature forging, medium-temperature forging and low-temperature forging in a gradient manner to improve the recrystallization volume fraction of the forging and reduce the strength difference and toughness difference between three directions, but the invention does not consider the structural uniformity of the aluminum alloy forging with larger thickness. Patent CN111644548A discloses a forging technology for forging a high-strength homogeneous aluminum alloy forging for aerospace, which reduces the generation of cracks in the forging process through upsetting and upsetting with multiple small deformations, but the invention does not relate to the improvement of stress corrosion performance.
Disclosure of Invention
Aiming at the defects of the prior art, the invention provides a high-strength corrosion-resistant aluminum alloy super-thick forging, and a preparation method and application thereof through component design, accurate control of a forging process and a novel aging treatment technology. The aluminum alloy forging has high strength, low stress corrosion sensitivity and good microstructure and performance uniformity, does not contain rare noble metal elements such as Sc and the like, effectively reduces the production cost, and is suitable for bearing structural members of aviation equipment. The invention specifically comprises the following contents:
a preparation method of a high-strength corrosion-resistant aluminum alloy super-thick forging comprises the following steps:
(1) Homogenizing the aluminum alloy cast ingot to obtain an aluminum alloy blank;
(2) Forging the homogenized aluminum alloy blank: firstly, carrying out 1-2 times of wide upsetting deformation and 2-3 times of wide drawing on an aluminum alloy blank, and then carrying out 1-2 times of wide upsetting deformation and 7-9 times of wide drawing to obtain an ultra-thick forging with the thickness not less than 200mm; the reduction of the wide upsetting deformation is 20% -40%, the thickness of the aluminum alloy blank is reduced by 10% -15% after 1-pass wide drawing, and the reduction speeds of the wide upsetting and the wide drawing are less than or equal to 4 mm/s;
(3) Carrying out solution treatment on the super-thick forging obtained in the step (2) to obtain a forging blank;
(4) Cold deforming the forging blank subjected to the solution treatment in the step (3) to reduce residual stress;
(5) Carrying out three-stage artificial aging treatment on the forge piece blank after cold deformation within 30 days, wherein the temperature of the first-stage aging treatment is 115-125 ℃, and the heat preservation time is 4-8 hours; the temperature of the second-stage aging treatment is 152-157 ℃, and the heat preservation time is 12-24 hours; the temperature of the third-stage aging treatment is 110-130 ℃, and the heat preservation time is 6-24 h.
Preferably, the aluminum alloy cast ingot in the step (1) comprises the following components in percentage by weight: 7.3-7.7% of Zn, 1.4-1.6% of Mg, 1.9-2.2% of Cu, 0.08-0.12% of Zr, less than or equal to 0.08% of Fe, less than or equal to 0.04% of Si, less than or equal to 0.04% of Mn, less than or equal to 0.03% of Cr, less than or equal to 0.03% of Ti, less than or equal to 0.08% of Fe+Mn, and the balance of Al.
Preferably, the thickness of the aluminum alloy cast ingot in the step (1) is 450-550 mm.
Preferably, the feeding amount of the wide-direction drawing in the step (2) is set as follows: when the length of the aluminum alloy blank in the width direction is smaller than 1000mm, controlling the feeding amount of the wide-direction drawing to be 250-300 mm; when the length of the aluminum alloy blank in the width direction is more than 1000mm and less than 1500mm, controlling the feeding amount of the wide-direction drawing to be 200-250 mm; when the length of the aluminum alloy blank in the width direction is more than 1500mm, the feeding amount of the wide-direction drawing is controlled to be not more than 200mm.
Preferably, step (2) further comprises: before the first wide upsetting deformation, heating the aluminum alloy cast ingot to 400-430 ℃ and preserving heat for more than or equal to 350min.
Preferably, the heat preservation temperature of the solution treatment in the step (3) is 470-480 ℃.
Preferably, after the solid solution treatment and heat preservation in the step (3) are completed, quenching the forging blank, and controlling the water temperature of quenching to be 40-50 ℃.
Preferably, step (5): the temperature rising speed of the first-stage aging treatment is 10-30 ℃/h; the temperature rising speed of the second-stage aging treatment is 6-12 ℃/h; the third-stage aging treatment adopts a mode of rapidly cooling to an aging temperature or firstly cooling and then heating to the aging temperature, the cooling time is controlled to be 10-30 min in the mode of rapidly cooling to the aging temperature, and the cooling mode in the mode of firstly cooling and then heating to the aging temperature is air cooling, and the heating speed is 10-30 ℃/h.
The high-strength corrosion-resistant aluminum alloy super-thick forging prepared by the preparation method of the high-strength corrosion-resistant aluminum alloy super-thick forging.
The high-strength corrosion-resistant aluminum alloy super-thick forging provided by the invention has the advantages that the longitudinal tensile strength is more than or equal to 530MPa, the yield strength is more than or equal to 530MPa, the elongation is more than or equal to 10%, and the high-strength corrosion-resistant aluminum alloy super-thick forging is not cracked after being periodically soaked for 20 days under the stress condition of 241MPa according to GB/T22640-2008.
An application of the high-strength corrosion-resistant aluminum alloy super-thick forging in aerospace equipment.
The invention has the beneficial effects that:
(1) According to the aluminum alloy forging disclosed by the invention, the contents and the proportion of the main alloy elements Zn, mg and Cu are reasonably adjusted, so that the alloy is ensured to have higher strength, the content of Cu in a grain boundary precipitation phase is increased, the potential difference between the grain boundary phase and a matrix is reduced, the galvanic corrosion at the grain boundary is inhibited, and the stress corrosion resistance of the Al-Zn-Mg-Cu alloy is improved.
(2) The aluminum alloy super-thick forging provided by the invention has the advantages that the content and the proportion of Fe and Mn elements are controlled, so that the content of indissolvable coarse phases in the alloy is effectively reduced, corrosion cracking caused by indissolvable coarse phases is reduced, and the stress corrosion resistance is improved.
(3) According to the invention, a novel forging process of upsetting and thickness extension of the cast ingot is adopted, strain is transmitted from the core of the cast ingot to the surface layer of the cast ingot through innovatively distributing parameters such as the extension depression, the extension feed, the depression speed and the like, and uniform distribution is realized in the thickness direction of the cast ingot, so that the surface layer of the ultra-thick forging is finally ensured to have a crystal grain structure consistent with the core of a plate and uniform mechanical properties.
(4) The invention adopts a three-stage aging process different from the conventional one, and is applied to super-thick forgings, so that the stress corrosion resistance of the alloy is greatly improved on the premise of ensuring sufficient strength. The longitudinal, transverse and high-directional tensile strength of the Al-Zn-Mg-Cu alloy forging is 30-40MPa higher than the minimum strength of the AMS standard in the United states, and the Al-Zn-Mg-Cu alloy forging is not cracked after being periodically immersed for 20 days under the stress condition of 241MPa according to the stress corrosion test method of C annular test sample of aluminum alloy processed products of GB/T22640-2008, so that the performance requirement of the aluminum alloy for aviation structural members is met.
Drawings
FIG. 1 shows the homogenized structure of an aluminum alloy ingot in example 1 of the present invention;
FIG. 2 is a grain structure of an aluminum alloy super-thick forging in example 2 of the present invention;
FIG. 3 is a TEM structure of a grain boundary precipitation phase of an aluminum alloy super-thick forging in example 3 of the present invention;
FIG. 4 is a C-ring fracture of an aluminum alloy super-thick forging in example 1 of the present invention;
FIG. 5 is a C-ring fracture of an aluminum alloy super-thick forging in example 3 of the present invention;
FIG. 6 is a grain structure of an aluminum alloy super-thick forging in comparative example 2 of the present invention;
FIG. 7 is a C-ring fracture of the aluminum alloy super-thick forging of comparative example 1 of the present invention;
FIG. 8 is a C-ring fracture of the aluminum alloy super-thick forging of comparative example 3 of the present invention.
Detailed Description
The invention will be described in detail below with reference to the drawings and the detailed description. The embodiments shown below do not limit the inventive content described in the claims in any way. The whole contents of the constitution shown in the following examples are not limited to the solution of the invention described in the claims.
The invention relates to a high-strength corrosion-resistant aluminum alloy super-thick forging, which comprises the following components in percentage by weight: 7.3-7.7% of Zn, 1.4-1.6% of Mg, 1.9-2.2% of Cu, 0.08-0.12% of Zr, less than or equal to 0.08% of Fe, less than or equal to 0.04% of Si, less than or equal to 0.04% of Mn, less than or equal to 0.03% of Cr, less than or equal to 0.03% of Ti, and the balance of Al, wherein the total amount of Fe and Mn is not more than 0.08%.
The invention relates to a preparation method of a high-strength corrosion-resistant aluminum alloy super-thick forging piece, which comprises the following steps:
(1) Homogenizing an aluminum alloy cast ingot with the thickness of 450-550 mm;
(2) Forging the homogenized blank, comprising the following steps: heating to 400-430 ℃ before the aluminum alloy ingot is subjected to wide upsetting deformation, wherein the heat preservation time is more than or equal to 350 minutes; then, performing 1 time of wide upsetting deformation and 2-3 times of wide drawing on the cast ingot; then carrying out 1 time of wide upsetting deformation and 6-10 times of wide drawing; the reduction of the ingot casting for the wide upsetting deformation is 20% -40%; the thickness of the cast ingot is reduced by 10% -15% after 1-pass widthwise drawing, and the reduction speeds of widthwise upsetting and widthwise drawing are less than or equal to 4 mm/s; when the length of the ingot in the width direction is less than 1000mm, the drawing feeding amount in the width direction is 250-300 mm; when the length in the width direction is more than 1000mm and less than 1500mm, the drawing feeding amount in the width direction is 200-250 mm; when the length in the width direction is more than 1500mm, the drawing feed in the width direction is not more than 200mm; the thickness of the obtained ultra-thick forging is not less than 200mm;
(3) Carrying out solution treatment on the obtained ultra-thick forging, wherein the solution temperature is 470-480 ℃, and the quenching water temperature is controlled to be 40-50 ℃ after the solution heat preservation is completed;
(4) Carrying out cold deformation residual stress reduction on the cooled forging blank;
(5) Carrying out three-stage artificial aging treatment on the forge piece blank after cold deformation within 30 days, wherein the temperature rising speed of the first-stage aging is 10-30 ℃/h, the aging temperature is 120 ℃, and the heat preservation time is 4-8 h; the temperature rising speed of the second-stage aging is 6-12 ℃/h, the aging temperature is 152-157 ℃, and the heat preservation time is 12-24 h; the third-stage aging adopts a mode of quickly cooling to the aging temperature or heating after cooling, the cooling mode is air cooling, the heating speed is 10-30 ℃/h, the aging temperature is 110-130 ℃, and the heat preservation time is 6-24 h.
The preparation method of the high-strength corrosion-resistant aluminum alloy super-thick forging piece provided by the invention follows the principle that:
(1) The aluminum alloy forging of the invention is manufactured by reasonably adjusting the main alloy elementThe content of Zn, mg and Cu ensures enough MgZn 2 The phase precipitation ensures that the alloy has higher strength, increases the content of Cu element in the grain boundary precipitation phase, reduces the potential difference between the grain boundary phase and the matrix, and improves the stress corrosion resistance of the Al-Zn-Mg-Cu alloy.
(2) The aluminum alloy super-thick forging provided by the invention has the advantages that the content of Fe and Mn elements is controlled, so that the content of indissolvable coarse phases in the alloy is effectively reduced, corrosion cracking caused by indissolvable coarse phases is reduced, and the stress corrosion resistance is improved.
(3) According to the invention, a novel forging process of upsetting and thickness extension of the cast ingot is adopted, strain is transmitted from the core of the cast ingot to the surface layer of the cast ingot through innovatively distributing parameters such as the extension depression, the extension feeding quantity, the depression speed and the like, and uniform distribution is realized in the thickness direction of the cast ingot, so that the surface layer of the ultra-thick forging is finally ensured to have a crystal grain structure consistent with the core of a plate and uniform mechanical properties.
(4) The invention adopts a three-stage aging process different from the conventional one, is applied to super-thick forgings, and forms high-density tiny MgZn in crystals by the first-stage aging and the second-stage aging 2 Phase, mgZn with intermittent distribution formed on grain boundary 2 And the Zn and Mg elements in the matrix are further separated out by the third-stage aging, so that the stress corrosion resistance of the alloy is greatly improved on the premise of ensuring sufficient strength.
A preparation method of a high-strength corrosion-resistant aluminum alloy super-thick forging comprises the following steps:
(1) Homogenizing an aluminum alloy ingot with the thickness of 450-550 mm (such as 420mm, 440mm, 460mm, 480mm, 500mm, 520mm, 540mm and the like) to obtain an aluminum alloy blank, wherein the aluminum alloy ingot comprises the following components in percentage by weight: 7.3-7.7% of Zn, 1.4-1.6% of Mg, 1.9-2.2% of Cu, 0.08-0.12% of Zr, less than or equal to 0.08% of Fe, less than or equal to 0.04% of Si, less than or equal to 0.04% of Mn, less than or equal to 0.03% of Cr, less than or equal to 0.03% of Ti, and less than or equal to 0.08% of Fe+Mn; specifically, the Zn content in the alloy may be 7.3%, 7.4%, 7.5%, 7.6%, 7.7%, etc.; mg content may be 1.4%, 1.45%, 1.5%, 1.55%, 1.6%, etc.; the Cu content may be 1.9%, 1.95%, 2.0%, 2.1%, 2.15%, etc.; the Zr content may be 0.09%, 0.095%, 0.10%, 0.11%, etc.; the Fe content may be 0, 0.01%, 0.02%, 0.04%, 0.06%, 0.07%, etc.; si content may be 0, 0.01%, 0.02%, 0.03%, etc.; mn content may be 0, 0.01%, 0.02%, 0.03%, etc.; the Cr content may be 0, 0.01%, 0.015%, 0.02%, 0.025%, etc.; the Ti content may be 0, 0.01%, 0.015%, 0.02%, 0.025%, etc.
(2) Forging the homogenized aluminum alloy blank: firstly heating the aluminum alloy ingot to 400-430 ℃ (for example, 405 ℃, 410 ℃, 415 ℃, 420 ℃, 425 ℃ and the like), keeping the temperature for more than or equal to 350min (for example, 360min, 370min, 380min, 400min, 450min and the like), then performing 1-2 times (preferably 1 time) of wide upsetting deformation and 2-3 times of wide drawing, and then performing 1-2 times (preferably 1 time) of wide upsetting deformation and 7-9 times of wide drawing to obtain an ultra-thick forge piece with the thickness not less than 200mm; the reduction of the wide upsetting deformation is 20% -40% (such as 22%, 24%, 26%, 28%, 30%, 32%, 35%, 38%, etc.), the thickness of the aluminum alloy blank is reduced by 10% -15% (such as 11%, 12%, 13%, 14%, etc.) every time the aluminum alloy blank is subjected to 1-pass wide drawing, and the reduction speeds of the wide upsetting and the wide drawing are less than or equal to 4 mm/s (such as 1mm/s, 1.5mm/s, 2mm/s, 2.5mm/s, 3mm/s, 3.5mm/s, etc.); the feeding amount of the wide-direction drawing is set as follows: when the length of the aluminum alloy blank in the width direction is smaller than 1000mm, controlling the feeding amount of the wide drawing to be 250-300 mm (for example, 260mm, 270mm, 280mm, 290mm and the like); when the length of the aluminum alloy blank in the width direction is more than 1000mm and less than 1500mm, controlling the feeding amount of the wide drawing to be 200-250 mm (for example, 210mm, 220mm, 230mm, 240mm and the like); when the length of the aluminum alloy blank in the width direction is more than 1500mm, controlling the feeding amount of the wide drawing to be not more than 200mm (for example, 100mm, 120mm, 150mm, 160mm, 180mm, 190mm and the like);
(3) Carrying out solution treatment on the ultra-thick forging obtained in the step (2), wherein the heat preservation temperature is 470-480 ℃ (such as 470 ℃, 472 ℃, 474 ℃, 476 ℃ and 478 ℃), and the like, so as to obtain a forging blank; then quenching the forging blank, and controlling the water temperature of quenching to be 40-50 ℃ (e.g. 42 ℃, 44 ℃, 46 ℃, 48 ℃ and the like);
(4) Cold deforming the forging blank subjected to the solution treatment in the step (3) to reduce residual stress;
(5) Carrying out three-stage artificial aging treatment on the forge piece blank after cold deformation within 30 days, wherein the heating rate of the first-stage aging treatment is 10-30 ℃/h (such as 12 ℃/h, 15 ℃/h, 18 ℃/h, 20 ℃/h, 22 ℃/h, 25 ℃/h, 28 ℃/h and the like), the temperature is 115-125 ℃ (such as 115 ℃, 118 ℃, 120 ℃, 122 ℃, 124 ℃ and the like), and the heat preservation time is 4-8 h (such as 4.5h, 5h, 5.5h, 6h, 6.5h, 7h, 7.5h and the like); the second-stage aging treatment has a heating rate of 6-12 ℃/h (e.g., 7 ℃/h, 8 ℃/h, 9 ℃/h, 10 ℃/h, 11 ℃/h, etc.), a temperature of 152-157 ℃ (e.g., 153 ℃, 154 ℃, 155 ℃, 156 ℃, etc.), and a heat preservation time of 12-24 hours (e.g., 14 ℃/h, 16 ℃/h, 18 ℃/h, 20 ℃/h, 22 ℃/h, etc.); the temperature of the third-stage aging treatment is 110-130 ℃ (for example, 112 ℃, 115 ℃, 118 ℃, 120 ℃, 122 ℃, 125 ℃, 128 ℃ and the like), the heat preservation time is 6-24 hours (for example, 8 hours, 10 hours, 12 hours, 15 hours, 18 hours, 20 hours, 22 hours and the like), the third-stage aging treatment adopts a mode of rapidly cooling down to the aging temperature or firstly cooling down and then heating up to the aging temperature, the cooling down time of the rapid cooling down to the aging temperature is controlled to be 10-30 minutes (for example, 12 minutes, 15 minutes, 18 minutes, 20 minutes, 22 minutes, 25 minutes, 28 minutes and the like), and the cooling down mode in the mode of firstly cooling down and then heating up to the aging temperature is air cooling, the heating up speed is 10-30 ℃/h (for example, 12 ℃/h, 15 ℃/h, 18 ℃/h, 20 ℃/h, 22 ℃/h, 25 ℃/h, 28 ℃/h and the like).
Preferred embodiments of the present invention will be described in detail below. The following examples and comparative examples are only for illustration of the present invention, but are not intended to limit the scope of the present invention.
Example 1
The Al-Zn-Mg-Cu alloy used in the embodiment comprises the following components in percentage by weight: 7.3% of Zn, 1.4% of Mg, 1.9% of Cu, 0.1% of Zr, 0.05% of Fe, 0.03% of Si, 0.03% of Mn, 0.02% of Cr, 0.01% of Ti, less than or equal to 0.08% of Fe+Mn and the balance of Al.
Homogenizing an ingot of aluminum alloy, and forging the soaked ingot, wherein the process is as follows:
(1) Sawing cast ingot: cutting an ingot of length 2000 mm x width 1200 mm x thickness 470 mm;
(2) Ingot casting and mold heating: heating the cast ingot to 400 ℃ and heating the die to 400 ℃;
(3) Forging: carrying out 1 st wide upsetting deformation on the cast ingot, wherein the deformation is 40%; then 2 times of drawing is carried out along the width direction, and the rolling reduction is 15 percent and 15 percent in sequence; then, the 2 nd wide upsetting is carried out, and the deformation is 25%; then 7 times of drawing is carried out along the width direction, and the rolling reduction is 15 percent; the thickness of the obtained ultra-thick forging piece is 218mm;
(4) Carrying out solution treatment on the forged blank, wherein the solution temperature is 475 ℃ and the time is 4h, and the quenching water temperature is controlled to be 45 ℃ after the solution treatment is completed;
(5) Carrying out cold deformation residual stress reduction on the cooled forging blank;
(6) And (3) heat treatment: carrying out three-stage artificial aging treatment on the cold deformed blank, wherein the first-stage aging temperature is 120 ℃, and preserving heat for 6 hours; the second-stage aging temperature is 155 ℃, and the heat preservation is carried out for 16 hours; the third stage aging temperature is 120 ℃, and the temperature is kept for 24 hours.
Example 2
The Al-Zn-Mg-Cu alloy used in the embodiment comprises the following components in percentage by weight: 7.7% of Zn, 1.6% of Mg, 2.2% of Cu, 0.1% of Zr, 0.06% of Fe, 0.04% of Si, 0.02% of Mn, 0.01% of Cr, 0.01% of Ti, less than or equal to 0.08% of Fe+Mn and the balance of Al.
Homogenizing an ingot of aluminum alloy, and forging the soaked ingot, wherein the process is as follows:
(1) Sawing cast ingot: cutting an ingot of length 2000 mm x width 1200 mm x thickness 470 mm;
(2) Ingot casting and mold heating: heating the cast ingot to 400 ℃ and heating the die to 400 ℃;
(3) Forging: carrying out 1 st wide upsetting deformation on the cast ingot, wherein the deformation is 20%; then 2 times of drawing is carried out along the width direction, and the rolling reduction is 15 percent and 15 percent in sequence; then, the 2 nd wide upsetting is carried out, and the deformation is 30%; then performing 9-pass drawing along the width direction, wherein the rolling reduction is 15%, 13%, 10% in sequence; obtaining the thickness of the ultra-thick forging piece to be 211mm;
(4) Carrying out solution treatment on the forged blank, wherein the solution temperature is 475 ℃ and the time is 4h, and the quenching water temperature is controlled to be 45 ℃ after the solution treatment is completed;
(5) Carrying out cold deformation residual stress reduction on the cooled forging blank;
(6) And (3) heat treatment: carrying out three-stage artificial aging treatment on the cold deformed blank, wherein the first-stage aging temperature is 120 ℃, and preserving heat for 6 hours; the second-stage aging temperature is 155 ℃, and the heat preservation is carried out for 16 hours; the third stage aging temperature is 120 ℃, and the temperature is kept for 24 hours.
Example 3
The Al-Zn-Mg-Cu alloy used in the embodiment comprises the following components in percentage by weight: 7.5% of Zn, 1.5% of Mg, 2.1% of Cu, 0.1% of Zr, 0.04% of Fe, 0.02% of Si, 0.02% of Mn, 0.02% of Cr, 0.01% of Ti, less than or equal to 0.08% of Fe+Mn and the balance of Al.
Homogenizing an ingot of aluminum alloy, and forging the soaked ingot, wherein the process is as follows:
(1) Sawing cast ingot: cutting an ingot of length 2000 mm x width 1200 mm x thickness 470 mm;
(2) Ingot casting and mold heating: heating the cast ingot to 400 ℃ and heating the die to 400 ℃;
(3) Forging: carrying out 1 st wide upsetting deformation on the cast ingot, wherein the deformation is 40%; then 3 times of drawing is carried out along the width direction, and the rolling reduction is 15%, 10% and 10% in sequence; then, the 2 nd wide upsetting is carried out, and the deformation is 20%; then 8 times of drawing is carried out along the width direction, and the rolling reduction is 15%, 13%, 10% and 10% in sequence; the thickness of the obtained ultra-thick forging piece is 207mm;
(4) Carrying out solution treatment on the forged blank, wherein the solution temperature is 475 ℃ and the time is 4h, and the quenching water temperature is controlled to be 45 ℃ after the solution treatment is completed;
(5) Carrying out cold deformation residual stress reduction on the cooled forging blank;
(6) And (3) heat treatment: carrying out three-stage artificial aging treatment on the cold deformed blank, wherein the first-stage aging temperature is 120 ℃, and preserving heat for 8 hours; the second-stage aging temperature is 152 ℃, and the heat preservation is carried out for 22 hours; the third stage aging temperature is 110 ℃, and the temperature is kept for 6 hours.
Example 4
The Al-Zn-Mg-Cu alloy used in the embodiment comprises the following components in percentage by weight: 7.5% of Zn, 1.5% of Mg, 2.1% of Cu, 0.1% of Zr, 0.05% of Fe, 0.03% of Si, 0.01% of Mn, 0.03% of Cr, 0.01% of Ti, less than or equal to 0.08% of Fe+Mn and the balance of Al.
Homogenizing an ingot of aluminum alloy, and forging the soaked ingot, wherein the process is as follows:
(1) Sawing cast ingot: cutting an ingot of length 2000 mm x width 1200 mm x thickness 470 mm;
(2) Ingot casting and mold heating: heating the cast ingot to 400 ℃ and heating the die to 400 ℃;
(3) Forging: carrying out 1 st wide upsetting deformation on the cast ingot, wherein the deformation is 40%; then 3 times of drawing is carried out along the width direction, and the rolling reduction is 15%, 10% and 10% in sequence; then, the 2 nd wide upsetting is carried out, and the deformation is 20%; then 8 times of drawing is carried out along the width direction, and the rolling reduction is 15%, 13%, 10% and 10% in sequence; the thickness of the obtained ultra-thick forging piece is 207mm;
(4) Carrying out solution treatment on the forged blank, wherein the solution temperature is 475 ℃ and the time is 4h, and the quenching water temperature is controlled to be 45 ℃ after the solution treatment is completed;
(5) Carrying out cold deformation residual stress reduction on the cooled forging blank;
(6) And (3) heat treatment: carrying out three-stage artificial aging treatment on the cold deformed blank, wherein the first-stage aging temperature is 120 ℃, and preserving heat for 4 hours; the second-stage aging temperature is 157 ℃, and the temperature is kept for 12 hours; the third stage aging temperature is 130 ℃, and the temperature is kept for 18 hours.
Comparative example 1
The Al-Zn-Mg-Cu alloy used in the embodiment comprises the following components in percentage by weight: 7.5% of Zn, 1.6% of Mg, 1.7% of Cu, 0.1% of Zr, 0.04% of Fe, 0.02% of Si, 0.03% of Mn, 0.02% of Cr, 0.01% of Ti, less than or equal to 0.08% of Fe+Mn and the balance of Al.
Homogenizing an ingot of aluminum alloy, and forging the soaked ingot, wherein the process is as follows:
(1) Sawing cast ingot: cutting an ingot of length 2000 mm x width 1200 mm x thickness 470 mm;
(2) Ingot casting and mold heating: heating the cast ingot to 400 ℃ and heating the die to 400 ℃;
(3) Forging: carrying out 1 st wide upsetting deformation on the cast ingot, wherein the deformation is 40%; then 3 times of drawing is carried out along the width direction, and the rolling reduction is 15%, 10% and 10% in sequence; then, the 2 nd wide upsetting is carried out, and the deformation is 20%; then 8 times of drawing is carried out along the width direction, and the rolling reduction is 15%, 13%, 10% and 10% in sequence; the thickness of the obtained ultra-thick forging piece is 207mm;
(4) Carrying out solution treatment on the forged blank, wherein the solution temperature is 475 ℃ and the time is 4h, and the quenching water temperature is controlled to be 45 ℃ after the solution treatment is completed;
(5) Carrying out cold deformation residual stress reduction on the cooled forging blank;
(6) And (3) heat treatment: carrying out three-stage artificial aging treatment on the cold deformed blank, wherein the first-stage aging temperature is 120 ℃, and preserving heat for 6 hours; the second-stage aging temperature is 155 ℃, and the heat preservation is carried out for 16 hours; the third stage aging temperature is 110 ℃, and the temperature is kept for 6 hours.
Comparative example 2
The Al-Zn-Mg-Cu alloy used in the embodiment comprises the following components in percentage by weight: 7.5% of Zn, 1.5% of Mg, 2.1% of Cu, 0.1% of Zr, 0.04% of Fe, 0.02% of Si, 0.03% of Mn, 0.02% of Cr, 0.01% of Ti, less than or equal to 0.08% of Fe+Mn and the balance of Al.
Homogenizing an ingot of aluminum alloy, and forging the soaked ingot, wherein the process is as follows:
(1) Sawing cast ingot: cutting an ingot of length 2000 mm x width 1200 mm x thickness 470 mm;
(2) Ingot casting and mold heating: heating the cast ingot to 400 ℃ and heating the die to 400 ℃;
(3) Forging: carrying out wide upsetting deformation on the cast ingot, wherein the deformation is 60%; then performing 9-pass drawing along the width direction, wherein the rolling reduction is 25%, 20%, 15% and 11% in sequence; the thickness of the obtained ultra-thick forging piece is 207mm;
(4) Carrying out solution treatment on the forged blank, wherein the solution temperature is 475 ℃ and the time is 4h, and the quenching water temperature is controlled to be 45 ℃ after the solution treatment is completed;
(5) Carrying out cold deformation residual stress reduction on the cooled forging blank;
(6) And (3) heat treatment: carrying out three-stage artificial aging treatment on the cold deformed blank, wherein the first-stage aging temperature is 120 ℃, and preserving heat for 6 hours; the second-stage aging temperature is 155 ℃, and the heat preservation is carried out for 22 hours; the third stage aging temperature is 120 ℃, and the temperature is kept for 24 hours.
Comparative example 3
The Al-Zn-Mg-Cu alloy used in the embodiment comprises the following components in percentage by weight: 7.5% of Zn, 1.5% of Mg, 2.1% of Cu, 0.1% of Zr, 0.05% of Fe, 0.03% of Si, 0.02% of Mn, 0.01% of Cr, 0.01% of Ti, less than or equal to 0.08% of Fe+Mn and the balance of Al.
Homogenizing an ingot of aluminum alloy, and forging the soaked ingot, wherein the process is as follows:
(1) Sawing cast ingot: cutting an ingot of length 2000 mm x width 1200 mm x thickness 470 mm;
(2) Ingot casting and mold heating: heating the cast ingot to 400 ℃ and heating the die to 400 ℃;
(3) Forging: carrying out 1 st wide upsetting deformation on the cast ingot, wherein the deformation is 40%; then 2 times of drawing is carried out along the width direction, and the rolling reduction is 15 percent and 15 percent in sequence; then, the 2 nd wide upsetting is carried out, and the deformation is 25%; then 7 times of drawing is carried out along the width direction, and the rolling reduction is 15 percent; the thickness of the obtained ultra-thick forging piece is 218mm;
(4) Carrying out solution treatment on the forged blank, wherein the solution temperature is 475 ℃ and the time is 4h, and the quenching water temperature is controlled to be 45 ℃ after the solution treatment is completed;
(5) Carrying out cold deformation residual stress reduction on the cooled forging blank;
(6) And (3) heat treatment: carrying out secondary artificial aging treatment on the blank after cold deformation, wherein the primary aging temperature is 120 ℃, and preserving heat for 6 hours; the second stage aging temperature is 155 ℃, and the heat preservation is carried out for 16 hours.
Referring to table 1, the ultra-thick forgings prepared in the examples and comparative examples of the present invention have room temperature tensile properties, electrical conductivity and stress corrosion properties. The room temperature tensile properties, conductivity and stress corrosion properties of the examples in table 1 are significantly better than those of the comparative examples.
FIG. 1 shows the homogenized structure of an aluminum alloy ingot in example 1; FIG. 2 is a grain structure of an aluminum alloy super-thick forging of example 2; FIG. 6 is a grain structure of an aluminum alloy super-thick forging in comparative example 2. According to the invention, a novel forging process of upsetting and direct drawing of thickness of the cast ingot is adopted, parameters such as drawing depression, drawing feeding quantity, pressing speed and the like are innovatively distributed, so that the final forging is uniformly distributed in the thickness direction of the cast ingot, and the surface layer of the plate is ensured to have a crystal grain structure consistent with the core of the plate and uniform mechanical properties.
FIG. 3 is a TEM structure of a grain boundary precipitation phase of an aluminum alloy super-thick forging in example 3; according to the invention, the main alloy element contents of Zn, mg and Cu are reasonably regulated, so that the alloy is ensured to be at a high strength level, meanwhile, the Cu element content is optimized, the Cu element content of a grain boundary precipitation phase is improved, the potential difference between a matrix and the grain boundary phase is reduced, and the stress corrosion performance of the alloy is improved.
FIG. 4 is a stress corrosion test C-ring fracture of an aluminum alloy super-thick forging of example 1; FIG. 5 is a stress corrosion test C-ring fracture of an aluminum alloy super-thick forging of example 3; FIG. 7 is a stress corrosion test C-ring fracture of the aluminum alloy super-thick forging of comparative example 1; FIG. 8 is a stress corrosion test C-ring fracture of an aluminum alloy super-thick forging of comparative example 3. In the embodiment, after the stress corrosion test C ring is soaked, the surface is visually observed to be mainly provided with corrosion pits, no cracks exist, after the section of the stress corrosion test C ring is cut, the section of the fracture is metallographic observed, the depth of the corrosion pits is within the range of 0.1-0.5 mm, and the stress corrosion performance is judged to be excellent; in the comparative example, after the stress corrosion test C ring is soaked, a large number of short cracks appear on the surface of the C ring, and after the section of the C ring is cut through the stress corrosion test C ring, metallographic observation is carried out on the section of the fracture, the depth of a corrosion pit is within the range of 1.5-2 mm, and the failure of the stress corrosion performance is judged.
The foregoing is merely a specific application example of the present invention, and the protection scope of the present invention is not limited in any way. All technical schemes formed by equivalent transformation or equivalent substitution fall within the protection scope of the invention.
Table 1 properties of aluminum alloy forgings of examples and comparative examples
The previous description of the disclosed embodiments is provided to enable any person skilled in the art to make or use the present invention. Various modifications to these embodiments will be readily apparent to those skilled in the art, and the generic principles defined herein may be applied to other embodiments without departing from the spirit or scope of the invention. Thus, the present invention is not intended to be limited to the embodiments shown herein but is to be accorded the widest scope consistent with the principles and novel features disclosed herein.
Claims (11)
1. The preparation method of the high-strength corrosion-resistant aluminum alloy super-thick forging piece is characterized by comprising the following steps of:
(1) Homogenizing the aluminum alloy cast ingot to obtain an aluminum alloy blank;
(2) Forging the homogenized aluminum alloy blank: firstly, carrying out 1-2 times of wide upsetting deformation and 2-3 times of wide drawing on an aluminum alloy blank, and then carrying out 1-2 times of wide upsetting deformation and 7-9 times of wide drawing to obtain an ultra-thick forging with the thickness not less than 200mm; the reduction of the wide upsetting deformation is 20% -40%, the thickness of the aluminum alloy blank is reduced by 10% -15% after 1-pass wide drawing, and the reduction speeds of the wide upsetting and the wide drawing are less than or equal to 4 mm/s;
(3) Carrying out solution treatment on the super-thick forging obtained in the step (2) to obtain a forging blank;
(4) Cold deforming the forging blank subjected to the solution treatment in the step (3) to reduce residual stress;
(5) Carrying out three-stage artificial aging treatment on the forge piece blank after cold deformation within 30 days, wherein the temperature of the first-stage aging treatment is 115-125 ℃, and the heat preservation time is 4-8 hours; the temperature of the second-stage aging treatment is 152-157 ℃, and the heat preservation time is 12-24 hours; the temperature of the third-stage aging treatment is 110-130 ℃, and the heat preservation time is 6-24 h.
2. The method for preparing the high-strength corrosion-resistant aluminum alloy super-thick forging piece according to claim 1, wherein the components and weight percentages of the aluminum alloy cast ingot in the step (1) are as follows: 7.3-7.7% of Zn, 1.4-1.6% of Mg, 1.9-2.2% of Cu, 0.08-0.12% of Zr, less than or equal to 0.08% of Fe, less than or equal to 0.04% of Si, less than or equal to 0.04% of Mn, less than or equal to 0.03% of Cr, less than or equal to 0.03% of Ti, less than or equal to 0.08% of Fe+Mn, and the balance of Al.
3. The method for manufacturing the high-strength corrosion-resistant aluminum alloy super-thick forging piece according to claim 1, wherein the thickness of the aluminum alloy cast ingot in the step (1) is 450-550 mm.
4. The method for manufacturing a super-thick aluminum alloy forging with high strength and corrosion resistance according to claim 1, wherein the feeding amount of the wide-direction drawing in the step (2) is set as follows: when the length of the aluminum alloy blank in the width direction is smaller than 1000mm, controlling the feeding amount of the wide-direction drawing to be 250-300 mm; when the length of the aluminum alloy blank in the width direction is more than 1000mm and less than 1500mm, controlling the feeding amount of the wide-direction drawing to be 200-250 mm; when the length of the aluminum alloy blank in the width direction is more than 1500mm, the feeding amount of the wide-direction drawing is controlled to be not more than 200mm.
5. The method for manufacturing a high-strength corrosion-resistant aluminum alloy super-thick forging according to claim 1, wherein the step (2) further comprises: before the first wide upsetting deformation, heating the aluminum alloy cast ingot to 400-430 ℃ and preserving heat for more than or equal to 350min.
6. The method for preparing the high-strength corrosion-resistant aluminum alloy super-thick forging according to claim 1, wherein the heat preservation temperature of the solution treatment in the step (3) is 470-480 ℃.
7. The method for preparing the high-strength corrosion-resistant aluminum alloy super-thick forging piece according to claim 1, wherein after the solution treatment and heat preservation in the step (3) are completed, the forging piece blank is subjected to quenching treatment, and the water temperature of quenching is controlled to be 40-50 ℃.
8. The method for manufacturing a high-strength aluminum alloy super-thick forging according to claim 1, wherein the step (5) is as follows: the temperature rising speed of the first-stage aging treatment is 10-30 ℃/h; the temperature rising speed of the second-stage aging treatment is 6-12 ℃/h; the third-stage aging treatment adopts a mode of rapidly cooling to an aging temperature or firstly cooling and then heating to the aging temperature, the cooling time is controlled to be 10-30 min in the mode of rapidly cooling to the aging temperature, and the cooling mode in the mode of firstly cooling and then heating to the aging temperature is air cooling, and the heating speed is 10-30 ℃/h.
9. A high-strength corrosion-resistant aluminum alloy super-thick forging prepared by the method for preparing the high-strength corrosion-resistant aluminum alloy super-thick forging according to any one of claims 1 to 8.
10. The high-strength corrosion-resistant aluminum alloy super-thick forge piece according to claim 9, wherein the longitudinal tensile strength is greater than or equal to 530MPa, the yield strength is greater than or equal to 530MPa, the elongation is greater than or equal to 10%, and the super-thick forge piece is free from cracking after being periodically immersed for 20 days under the stress condition of 241MPa according to GB/T22640-2008.
11. Use of the high-strength corrosion-resistant aluminum alloy super-thick forging as set forth in claim 9 in aerospace equipment.
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