CN114737142B - Low-stress corrosion-resistant preparation method for aluminum alloy casting through vibratory aging and cryogenic treatment - Google Patents

Low-stress corrosion-resistant preparation method for aluminum alloy casting through vibratory aging and cryogenic treatment Download PDF

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CN114737142B
CN114737142B CN202210659262.3A CN202210659262A CN114737142B CN 114737142 B CN114737142 B CN 114737142B CN 202210659262 A CN202210659262 A CN 202210659262A CN 114737142 B CN114737142 B CN 114737142B
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treatment
aluminum alloy
alloy casting
temperature
heat treatment
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CN114737142A (en
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樊振中
洪润洲
师可馨
王建国
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AECC Beijing Institute of Aeronautical Materials
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AECC Beijing Institute of Aeronautical Materials
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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
    • 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
    • C22F1/002—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
    • 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
    • C22F3/00—Changing the physical structure of non-ferrous metals or alloys by special physical methods, e.g. treatment with neutrons
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/20—Recycling

Abstract

The invention provides a low-stress corrosion-resistant preparation method for a high-toughness aluminum alloy casting through vibration aging and cryogenic treatment. The invention adopts a vibration aging process to eliminate the quenching residual stress of the aluminum alloy casting, combines size stabilization treatment to ensure the overall size precision of the aluminum alloy casting, utilizes primary cryogenic treatment to crush precipitation strengthening phases in the pre-aging heat treatment process, and adopts aging heat treatment and secondary cryogenic treatment to improve the precipitation morphology, the quantity, the size and the distribution density of the precipitation strengthening phases, thereby improving the distribution morphology and the density of the precipitation strengthening phases along crystal boundaries to improve the mechanical property and the corrosion resistance of metal materials, and realizing the short-period, low-cost, high-toughness and high-precision corrosion-resistant heat treatment preparation of the high-toughness aluminum alloy casting in the field of military equipment and automobiles.

Description

Low-stress corrosion-resistant preparation method for aluminum alloy casting through vibratory aging and cryogenic treatment
Technical Field
The invention belongs to the field of aluminum alloy technology and process method, and particularly relates to a vibration aging and cryogenic treatment low-stress corrosion-resistant preparation method for a high-strength and high-toughness aluminum alloy casting.
Background
The aluminum alloy has the advantages of low density, high specific strength/rigidity, good corrosion resistance, good plasticity, excellent processing performance, good welding performance, excellent electrical conductivity and thermal conductivity, and is widely applied to the field of military equipment. The aluminum alloy can be mainly divided into wrought aluminum alloy and cast aluminum alloy according to the processing technology, wherein the cast aluminum alloy has good process flow property and medium load bearing capacity, and is widely applied to the manufacture of products such as missile shells, oil-carrying cabin shells, engine accessory casings, engine oil-way pipelines, automobile engine cylinder bodies, automobile engine cylinder covers and the like.
Aluminum alloy castings in the field of military equipment and the field of automobiles are mostly of complex thin-wall structures, warping or bending deformation is easy to generate under the influence of quenching residual stress in the quenching heat treatment process, castings are scrapped even directly in severe cases, most of traditional quenching residual stress eliminating process methods are thermal ageing methods, the process operation time is long, and the residual stress eliminating effect is general; the overlong aging heat preservation time also changes the precipitation form and distribution density of the precipitation strengthening phase of the metal material, and even deteriorates the mechanical property and the corrosion resistance of the metal material in severe cases.
With the continuous improvement of the requirement of military equipment field on the long-life reliable service technical index of the aluminum alloy casting, how to improve the mechanical property and the corrosion resistance of the aluminum alloy casting in the heat treatment process of the aluminum alloy casting on the premise of ensuring the integral size precision of the casting becomes one of the heat point research and process control difficulties in the current precision heat treatment field of the aluminum alloy casting. The hot spots of the current aluminum alloy casting heat treatment process research are mainly single research for improving the mechanical property of metal materials, eliminating quenching residual stress or carrying out size stabilization treatment. Therefore, from the perspective of operation technology, it is very important to comprehensively realize high strength and toughness, low stress and high corrosion resistance of the aluminum alloy casting.
Disclosure of Invention
The invention provides a vibration aging and cryogenic treatment low-stress corrosion-resistant preparation method for a high-strength and high-toughness aluminum alloy casting, aiming at the process problems of quenching deformation, low mechanical property, poor corrosion resistance and the like of the existing thin-wall complex-structure aluminum alloy casting for military equipment in the quenching heat treatment process. The two-stage solid solution heat preservation treatment process adopted by the invention improves the solid solution supersaturation degree of the alloy elements to the maximum extent; the spray quenching process adopted by the invention can reduce the action time of 'gas film isolated heat transfer' and 'bubble boiling heat transfer' in the traditional quenching heat treatment process, and can ensure that the whole size precision of the quenched casting meets the technical requirement of subsequent precision machining through thermal state mechanical correction; the pre-aging heat treatment can provide process guarantee for the effective implementation of subsequent vibration aging, and the combination of size stabilization treatment and primary cryogenic treatment and secondary cryogenic treatment can improve the distribution appearance, quantity, size and density of aging precipitation strengthening phases and the appearance distributed along grain boundaries while further reducing the quenching residual stress of castings, effectively improve the mechanical property and corrosion resistance of metal materials, and realize the short-period, low-cost, high-strength and high-toughness, high-corrosion-resistance precision heat treatment manufacturing of high-strength and high-toughness aluminum alloy castings for military tools.
The invention specifically provides the following technical scheme:
a method of making an aluminum alloy casting, the method comprising the steps of:
(1) secondary solid solution heat preservation treatment: placing the aluminum alloy casting in a solid solution heat preservation furnace for secondary solid solution heat preservation treatment;
(2) quenching heat treatment: placing the aluminum alloy casting subjected to the secondary solution heat-preservation heat treatment in a spray quenching furnace for spray quenching treatment, wherein spray heads symmetrically distributed along the aluminum alloy casting are installed in the spray quenching furnace, and the spray heads spray liquid quenching medium to carry out quenching heat treatment on the aluminum alloy casting;
(3) thermal state mechanical correction: scanning and analyzing the size of the sprayed and quenched aluminum alloy casting by adopting non-contact optical measuring equipment, and then carrying out thermal state correction on the aluminum alloy casting by using a mechanical correction device and a hydraulic device;
(4) pre-aging heat treatment: placing the aluminum alloy casting in an aging heat preservation furnace, and performing pre-aging heat preservation treatment;
(5) vibration aging treatment: after the pre-aging heat preservation heat treatment of the aluminum alloy casting is finished, taking the aluminum alloy casting out of the aging heat preservation furnace, and carrying out vibration aging treatment on the aluminum alloy casting;
(6) and (3) size stabilization treatment: placing the aluminum alloy casting subjected to the vibratory ageing treatment in a liquid nitrogen cold-state heat preservation furnace for size stabilization treatment;
(7) primary cryogenic treatment: after finishing size stabilization treatment, continuously placing the aluminum alloy casting in a liquid nitrogen cold-state heat preservation furnace for primary cryogenic treatment;
(8) aging heat treatment: placing the aluminum alloy casting subjected to primary subzero treatment in an aging heat treatment heat preservation furnace for aging heat treatment;
(9) secondary subzero treatment: and placing the aluminum alloy casting subjected to the aging heat treatment in a liquid nitrogen cold-state heat preservation furnace for secondary subzero treatment, and taking out the aluminum alloy casting after the secondary subzero treatment is finished, so as to finish the vibration aging and subzero treatment low-stress corrosion-resistant preparation of the high-strength and high-toughness aluminum alloy casting.
According to an embodiment of the present invention, in the step (1), the aluminum alloy casting is an aluminum silicon series aluminum alloy casting, an aluminum copper series aluminum alloy casting, or an aluminum magnesium series aluminum alloy casting.
According to the embodiment of the invention, in the step (1), the charging temperature of the aluminum alloy casting is less than or equal to 100 ℃, for example, 20 ℃ to 100 ℃.
According to an embodiment of the present invention, in the step (1), the temperature increase rate of the secondary solution heat-retention treatment is 2 ℃. min -1 ~3℃·min -1 (e.g., 2 ℃ C. min.) -1 、2.2℃·min -1 、2.5℃·min -1 、2.8℃·min -1 Or 3 ℃ min -1 ) The secondary solution heat-preservation heat treatment comprises a primary solution heat-preservation heat treatment and a secondary solution heat-preservation heat treatment, wherein the temperature of the primary solution heat-preservation heat treatment is (T) Melting temperature of eutectic phase with low melting point -10) DEG C, the time of the first stage solution heat-preservation heat treatment is 3 h-5 h (for example, 3h, 3.5h, 4h, 4.5h or 5 h), and the temperature of the second stage solution heat-preservation heat treatment is (T) Melting temperature of eutectic phase with low melting point -3) DEG C, and the time of the second-stage solution heat-preservation heat treatment is 12 h-16 h (for example, 12h, 13h, 14h, 15h or 16 h).
According to an embodiment of the present invention, said T Melting temperature of eutectic phase with low melting point Can be measured by DSC, TG, TMA and other material thermal analysis methods. Illustratively, the T is Melting temperature of eutectic phase with low melting point The temperature is 540 ℃ to 560 ℃.
According to the embodiment of the invention, in the step (1), the temperature uniformity control range of the solid solution holding furnace is +/-2 ℃.
According to an embodiment of the present invention, in step (2), the quench transfer time is ≦ 10 s.
According to the embodiment of the invention, in the step (2), the sprayed quenching medium is deionized water or polyethylene glycol or other organic quenching mediumThe spraying flow of the solvent and the spray header is 0.20 L.s -1 ~0.45L·s -1 (e.g., 0.2L · s) -1 、0.25L·s -1 、0.3L·s -1 、0.35L·s -1 、0.4L·s -1 Or 0.45L · s -1 ) The spraying time of the spray head is 5-15 min, the spraying angle of the spray head is-60 degrees to +60 degrees, and the diameter of a spraying opening of the spray head is 1.0-3.0 mm.
According to the embodiment of the invention, in the step (3), the detection light source of the non-contact optical measurement device is laser, the number of single scanning points is 600 ten thousand to 2000 ten thousand, the point spacing is 0.018mm to 0.037mm, and the precision of the measurement size is +/-0.001 mm.
According to the embodiment of the present invention, in the step (3), the material of the mechanical calibration device is a steel structure.
According to the embodiment of the invention, in the step (3), the hydraulic pressure provided by the hydraulic device is in a range of 1T-10T, such as 1T, 2T, 3T, 4T, 5T, 6T, 7T, 8T, 9T and 10T.
According to the embodiment of the invention, in the step (4), the charging temperature of the aluminum alloy casting is less than 50 ℃.
According to an embodiment of the present invention, in the step (4), the temperature increase rate of the pre-aging heat treatment is 1.2. degreeC.min -1 ~2.0℃·min -1 (e.g., 1.2 ℃ C. min) -1 、1.5℃·min -1 、1.6℃·min -1 、1.8℃·min -1 Or 2 ℃ min -1 ) The temperature of the pre-aging heat treatment is 140 ℃ to 180 ℃ (for example, 140 ℃, 150 ℃, 160 ℃, 170 ℃ or 180 ℃), and the temperature of the pre-aging heat treatment is 2h to 4h (for example, 2h, 2.5h, 3h, 3.5h or 4 h).
According to the embodiment of the invention, in the step (4), the temperature uniformity control range of the aging holding furnace is +/-5 ℃.
According to the embodiment of the invention, in the step (5), the aluminum alloy casting is subjected to residual stress detection before and after vibration aging treatment; the residual stress detection device of the aluminum alloy casting is X-ray residual stress detection equipment, grinding and polishing treatment needs to be carried out on a part to be detected of the aluminum alloy casting before testing, grinding abrasive paper is 200-2000 meshes, polishing paste used during polishing is 1500-6000 meshes, the measuring method is a tilting fixation method, radiation rays are Crk alpha, the voltage of an X-ray pipeline is 5-50 kV, the current of the X-ray pipeline is 5-30 mA, single-point testing time is 0.5-1.5 min, the 2 theta scanning starting angle is 170-140 degrees, and the 2 theta scanning stopping angle is 140-110 degrees.
According to the embodiment of the invention, in the step (5), the excitation frequency of the vibration aging heat treatment is 10 Hz-1000 Hz, and the rotation speed of the excitation motor is 1000r.min -1 ~10000r.min -1 The vibration acceleration of the exciting motor is 20m.s -2 ~100m.s -2 The exciting force is 500N-3000N, and the exciting time is 15 min-45 min.
According to the embodiment of the invention, in the step (6), the charging temperature of the aluminum alloy casting is less than 40 ℃.
According to the embodiment of the invention, in the step (6), the temperature uniformity of the liquid nitrogen cold-state holding furnace is controlled within the temperature range of +/-5 ℃.
According to an embodiment of the present invention, in the step (6), the temperature reduction rate of the dimensional stabilization treatment is-1.5. degreeCmin -1 ~-1.2℃·min -1 (e.g., -1.5 ℃ C. min -1 、-1.4℃·min -1 、-1.3℃·min -1 Or at-1.2 ℃ min -1 ) The temperature for the size stabilization treatment is-120 ℃ to-110 ℃ (for example, -120 ℃, 118 ℃, 116 ℃, 115 ℃, 114 ℃, 112 ℃ or-110 ℃), and the temperature for the size stabilization treatment is 20min to 40min (such as 20min, 25min, 30min, 35min or 40 min).
According to the embodiment of the invention, in the step (7), the temperature uniformity of the liquid nitrogen cold-state holding furnace is controlled within the temperature range of +/-5 ℃.
According to the embodiment of the present invention, in the step (7), the temperature reduction rate of the primary cryogenic treatment is-3.0 ℃ min -1 ~-2.0℃·min -1 (e.g., -2 ℃ C. min) -1 、-2.2℃·min -1 、-2.5℃·min -1 、-2.8℃·min -1 Or at-3 ℃ min -1 ) The heat preservation temperature of the primary deep cooling treatment is-180 ℃ to-170 ℃ (for example, -180 ℃, -179 ℃, -178 ℃, -176 ℃, -17 ℃)5 ℃, 174 ℃, 172 ℃, 171 ℃ or 170 ℃, and the heat preservation time of the primary deep cooling treatment is 40min to 60min (such as 40min, 45min, 50min, 55min or 60 min).
According to the embodiment of the invention, in the step (8), the charging temperature of the aluminum alloy casting is 20-40 ℃.
According to the embodiment of the present invention, in the step (8), the temperature increase rate of the aging heat treatment is 1.5 ℃ min -1 ~3.0℃·min -1 (e.g., 1.5 ℃ C. min) -1 、1.6℃·min -1 、1.8℃·min -1 、2℃·min -1 、2.2min -1 、2.5min -1 、2.8min -1 Or 3min -1 ) The heat preservation temperature of the aging heat treatment is 160 ℃ to 180 ℃ (for example, 160 ℃, 165 ℃, 170 ℃, 175 ℃ or 180 ℃), and the heat preservation time of the aging heat treatment is 4h to 6 h.
According to the embodiment of the invention, in the step (8), the temperature uniformity control range of the aging heat treatment holding furnace is +/-2 ℃.
According to the embodiment of the invention, in the step (9), the charging temperature of the aluminum alloy casting is less than 60 ℃.
According to the embodiment of the invention, in the step (9), the temperature uniformity of the liquid nitrogen cold-state holding furnace is controlled within the temperature range of +/-5 ℃.
According to the embodiment of the invention, in the step (9), the cooling rate of the secondary cryogenic treatment is-5.0 ℃ min -1 ~-3.0℃·min -1 (e.g., -5 ℃ C. min) -1 、-4.5℃·min -1 、-4℃·min -1 、-3.5℃·min -1 、-3℃·min -1 ) The heat preservation temperature of the secondary subzero treatment is-180 ℃ to-160 ℃ (for example, -160 ℃, 165 ℃, 170 ℃, 175 ℃ or-180 ℃), and the heat preservation time of the secondary subzero treatment is 20min to 30min (for example, 20min, 22min, 25min, 28min or 30 min).
According to the embodiment of the invention, in the step (9), after the secondary cryogenic treatment is finished, the aluminum alloy casting is discharged from the furnace and heated to the room temperature, for example, the aluminum alloy casting is placed at the room temperature and naturally heated to the room temperature.
Has the beneficial effects that:
the invention provides a low-stress corrosion-resistant preparation method for high-toughness aluminum alloy castings through vibratory stress relief and cryogenic treatment. Compared with the traditional heat treatment process, the method has the following distinct process advantages: (1) the solid solution heat preservation is a secondary solid solution heat preservation treatment, can obviously improve the solid solution supersaturation degree of alloy elements such as Mg, Cu, Ti, V, Cd and the like, and provides a chemical driving force for the high-density precipitation of a strengthening phase in the aging heat treatment process. (2) Compared with the traditional immersion quenching process, the quenching transfer time of the spray quenching heat treatment process is extremely short, the spray quenching can be adjusted by the spray angle of the spray header, the action time of 'gas film isolated heat transfer' and 'bubble boiling heat transfer' in the traditional immersion quenching heat treatment process is obviously shortened, and the problem of overhigh quenching residual stress caused by uneven quenching heat transfer of all parts of a casting in the traditional immersion quenching process can be effectively reduced to a certain extent on the basis of improving the solid solution supersaturation degree of alloy elements. (3) The whole temperature of the aluminum alloy casting after spray quenching is still high, the yield strength of the metal material is low, and the whole size precision of the aluminum alloy casting can be effectively ensured by timely thermal-state mechanical correction of the aluminum alloy casting by means of a mechanical correction device and a hydraulic device. (4) When the aluminum alloy material is in a solution quenching T4 heat treatment state, a large amount of alloy elements are dissolved in the primary alpha-Al matrix, so that good noise absorption and vibration reduction effects can be achieved, at the moment, the aluminum alloy casting is subjected to vibration aging, a large amount of vibration energy is absorbed by the metal material, and an effective stress elimination effect is difficult to achieve; when the metal material is in a T5/T6 heat treatment state, a large amount of precipitation strengthening phases are precipitated in the metal material, the yield strength of the metal material is high, the residual stress peak value superposed by vibration energy is difficult to exceed the yield strength of the metal material, and the stress relief effect of vibration aging is greatly reduced; therefore, the vibration aging of the aluminum alloy casting is selected to be carried out between the T4 heat treatment state and the T5/T6 heat treatment state, so that the quenching residual stress of the aluminum alloy casting can be effectively reduced or eliminated. (5) The peak value of the quenching residual stress of the aluminum alloy casting after the vibratory ageing is greatly reduced, the distribution and the severity of the quenching residual stress can be obviously improved, the overall dimensional precision of the aluminum alloy casting can be effectively stabilized by implementing the dimensional stabilization treatment, and the dimensional precision of the aluminum alloy casting is greatly improved. (6) In the process of pre-aging heat treatment, a certain amount of precipitated strengthening phases are precipitated in the aluminum alloy material and in the crystal boundary, and at the moment, the aluminum alloy casting is subjected to primary cryogenic treatment, so that precipitated strengthening phase particles can be effectively crushed under the action of internal stress of expansion with heat and contraction with cold, the amount of the precipitated strengthening phases is increased, and the strength and the plastic toughness of the metal material are improved; meanwhile, the appearance, the quantity and the density of precipitation strength distributed along the grain boundary are improved, the width of a non-precipitation zone of the grain boundary is increased, the potential difference between the interior of the grain and the grain boundary is reduced, and the corrosion resistance of the metal material is improved. (7) The aluminum alloy casting is subjected to secondary subzero treatment after the aging heat treatment is completed, and under the action of internal stress of expansion with heat and contraction with cold, some microscopic defects in the aluminum alloy casting can be effectively closed, so that the internal density of the metal material is improved, and the mechanical property and the corrosion resistance of the metal material are further improved on the premise of effectively ensuring the size precision of the aluminum alloy casting.
In conclusion, the invention adopts the vibration aging process to eliminate the quenching residual stress of the aluminum alloy casting, and simultaneously combines the size stabilizing treatment to ensure the overall size precision of the aluminum alloy casting, the precipitation strengthening phase in the pre-aging heat treatment process is crushed by means of primary cryogenic treatment, and the precipitation morphology, the quantity, the size and the distribution density of the precipitation strengthening phase are improved by adopting aging heat treatment and secondary cryogenic treatment, so that the distribution morphology and the density of the precipitation strengthening phase along the grain boundary are improved, the mechanical property and the corrosion resistance of the metal material are improved, and the short-period, low-cost, high-strength and high-toughness and high-corrosion-resistance precision heat treatment preparation of the high-strength and high-toughness aluminum alloy casting in the field of military equipment and automobiles is realized.
Drawings
FIG. 1 is a graph of time-temperature changes at various stages of the preparation process of example 1.
FIG. 2 is a schematic structural view of a ZL114A transition metal shell casting made in example 1.
FIG. 3 shows the results of the residual stress test of the ZL114A tail section metal shell casting of example 2 after quenching heat treatment and secondary sub-cooling treatment.
FIG. 4 shows the results of the dimensional measurements of the warpage of the ZL114A end section metal shell casting in example 2 after quenching heat treatment and secondary cryogenic treatment.
FIG. 5 shows TEM microstructure test results of the crystal interior and grain boundary of a ZL205A tail section metal shell casting compared with a traditional heat treatment process and the vibration aging and cryogenic treatment heat treatment process of the invention.
Fig. 6 is a schematic structural diagram of the mechanical correcting device.
FIG. 7 is a schematic illustration of structural positioning using a mechanical alignment device.
FIG. 8 is a schematic illustration of structural positioning using a mechanical alignment device.
FIG. 9 is a schematic illustration of structural positioning using a mechanical alignment device.
Reference numerals: 1 is a heat treatment supporting base, 2 is an excitation motor, 3 is a lower correcting frame, 4 is a correcting frame connecting nut, 5 is a correcting frame connecting screw rod, 6 is a correcting end conformal pressing block, 7 is a correcting end connecting rod, 8 is a correcting end bearing pressing plate, 9 is a correcting end limiting plate, 10 is a correcting end limiting plate connecting nut, 11 is a correcting end limiting plate connecting screw rod, 12 is a fixed end conformal pressing block, 13 is a fixed end inner limiting plate, 14 is a fixed end inner limiting plate connecting nut, 15 is a fixed end inner limiting plate connecting screw rod, 16 is a fixed end outer limiting plate, 17 is a fixed end limiting screw rod, 18 is a fixed end limiting screw rod stopping plate, 19 is a fixed end limiting screw rod stopping plate limiting nut, 20 is a fixed end outer limiting plate fastening screw rod, 21 is a fixed end outer limiting plate fastening nut, 22 is a lower correcting frame positioning clamping plate, 23 is an aluminum alloy casting, 24 is a middle correcting frame, 25 is a middle position correcting frame positioning clamping plate, 26 is an upper position correcting frame, 27 is a lower pressure table, and 28 is an upper pressure table.
Detailed Description
As described above, as shown in fig. 6 to 9, the mechanical correction device includes a heat treatment support base 1, a position correction frame positioning clamping plate, a position correction frame connecting nut 4, a position correction frame connecting screw 5, a correction end conformal pressing block 6, a correction end connecting rod 7, a correction end bearing plate 8, a correction end limiting plate 9, a correction end limiting plate connecting nut 10, a correction end limiting plate connecting screw 11, a fixed end conformal pressing block 12, a fixed end inner limiting plate 13, a fixed end inner limiting plate connecting nut 14, a fixed end inner limiting plate connecting screw 15, a fixed end outer limiting block 16, a fixed end limiting screw 17, a fixed end limiting screw stop plate 18, a fixed end limiting screw stop plate limiting nut 19, a fixed end outer limiting block fastening screw 20, and a fixed end outer limiting block fastening nut 21;
the position correcting frames comprise a lower position correcting frame 3, a middle position correcting frame 24 and an upper position correcting frame 26;
the positioning clamping plates of the positioning frame comprise a lower positioning clamping plate 22 and a middle positioning clamping plate 25;
the middle position correcting frame 24 is positioned above the lower position correcting frame 3 and is connected with the lower position correcting frame through a lower position correcting frame positioning clamping plate 22, and the upper position correcting frame 26 is positioned above the middle position correcting frame 24 and is connected with the middle position correcting frame through a middle position correcting frame positioning clamping plate 25;
the position correcting frame is a regular polygon formed by a first frame and a second frame;
the lower position-correcting frame 3 is positioned at the outer edge of the heat treatment supporting base 1, and the lower position-correcting frame 3 is in threaded connection with the heat treatment supporting base 1 through a position-correcting frame connecting nut 4 and a position-correcting frame connecting screw rod 5;
the correcting end limiting plate 9 is positioned at the outer edge of the first side frame of the correcting frame, and the correcting end limiting plate 9 is in threaded connection with the first side frame of the correcting frame through a correcting end limiting plate connecting nut 10 and a correcting end limiting plate connecting screw rod 11;
the correcting end shape-following pressing block 6 is connected with a correcting end pressure-bearing plate 8 through a correcting end connecting rod 7, the correcting end connecting rod 7 penetrates through a first frame of the correcting frame, the correcting end shape-following pressing block 6 is close to the inner edge side of the first frame of the correcting frame, and the correcting end pressure-bearing plate 8 is close to the outer edge side of the first frame of the lower correcting frame 3;
the fixed end outer limiting block 16 is positioned at the outer edge of the second frame of the position correcting frame, and the fixed end outer limiting block 16 is in threaded connection with the second frame of the position correcting frame through a fixed end outer limiting block fastening screw rod 20 and a fixed end outer limiting block fastening nut 21;
the fixed end inner limiting plate 13 is positioned at the inner edge of the second frame of the position correcting frame, and the fixed end inner limiting plate 13 is in threaded connection with the second frame of the position correcting frame through a fixed end inner limiting plate connecting nut 14 and a fixed end inner limiting plate connecting screw rod 15;
the stiff end is followed shape briquetting 12 and is ended the board 18 and stiff end limit screw and end board stop nut 19 and link to each other through stiff end limit screw 17, stiff end limit screw 17 passes the second frame of school position frame, stiff end is followed shape briquetting 12 and is close to the second frame inner edge side of school position frame, stiff end limit screw ends board 18 and stiff end limit screw and ends board stop nut 19 and is close to the second frame outer edge side of school position frame.
According to the embodiment of the invention, the mechanical correction device is used for mechanical correction of the aluminum alloy casting with the complex curved surface structure.
According to the embodiment of the invention, the material of the heat treatment supporting base 1 is medium carbon steel, cast iron or stainless steel.
The heat treatment supporting base 1 is in a wheel shape, the periphery of the heat treatment supporting base is provided with an annular groove, and a radiation linear structure is arranged in the heat treatment supporting base; the single-side thickness of the annular groove is more than or equal to 20 mm; the number of the radiant rays is 4-8, the width of the radiant line-shaped structure is larger than or equal to 60mm, and the height of the radiant line-shaped structure is larger than or equal to 40 mm.
The annular groove is in contact with the bottom surface of the aluminum alloy casting 23.
According to the embodiment of the invention, the position correcting frame is a regular hexagon, a regular octagon, a regular decagon or a regular dodecagon which is composed of the first frame and the second frame.
The number of the first frames of the position correcting frame is the same as the number of the second frames of the position correcting frame, the first frames are connected, and the second frames are connected.
The position correcting frame is made of low-carbon steel, medium-carbon steel or stainless steel.
The thickness of the first frame and the second frame of the position correcting frame is larger than or equal to 30mm, and the height of the first frame and the second frame of the position correcting frame is larger than or equal to 120 mm.
According to the embodiment of the invention, the positioning clamping plate of the positioning frame is made of low-carbon steel or medium-carbon steel.
The positioning clamping plate of the positioning frame is superposed with the top centers of the first frame and the second frame of the positioning frame.
The thickness of the positioning clamping plate of the positioning frame is more than or equal to 30 mm.
The number of the positioning clamping plates of the positioning frame is 1/2 of the number of the edges of the positioning frame.
According to the embodiment of the invention, the lower positioning frame positioning clamping plates 22 are arranged above the first frame and the second frame of the lower positioning frame 3 at intervals.
The lower position correcting frame positioning clamping plate 22 is superposed with the top centers of the first frame and the second frame of the lower position correcting frame 3.
The number of the lower positioning clamping plates 22 is 1/2 of the sum of the number of the first frames and the number of the second frames of the lower positioning frame 3.
The middle position correcting frame positioning clamping plates 25 are arranged above the first frame and the second frame of the lower position correcting frame 24 at intervals.
The middle position correcting frame positioning clamping plate 25 is superposed with the top centers of the first frame and the second frame of the lower position correcting frame 24.
The number of the middle position correcting frame positioning clamping plates 25 is 1/2 which is the sum of the number of the first frames and the number of the second frames of the middle position correcting frame 24.
The lower calibration frame 3, the middle calibration frame 24 and the upper calibration frame 26 have the same structure.
According to the embodiment of the invention, the lower alignment frame 3 and the heat treatment support base 1 are arranged in concentric circles.
According to the embodiment of the invention, the position correction frame connecting nut 4 and the position correction frame connecting screw rod 5 are made of low-carbon steel or stainless steel.
The first frame of each position correcting frame is in threaded connection with the heat treatment supporting base 1 through two position correcting frame connecting nuts 4 and two position correcting frame connecting screw rods 5; the second frame of each position correcting frame is in threaded connection with the heat treatment supporting base 1 through two position correcting frame connecting nuts 4 and two position correcting frame connecting screw rods 5.
The circle centers of the position correction frame connecting nut 4 and the position correction frame connecting screw rod 5 are overlapped and have the same number.
According to the embodiment of the invention, the correcting end conformal pressing block 6, the correcting end connecting rod 7 and the correcting end bearing plate 8 are made of stainless steel or die steel.
The circle centers of the correction end shape following pressing block 6, the correction end connecting rod 7 and the correction end bearing plate 8 are overlapped and have the same number.
The number of the correcting end shape following pressing blocks 6, the correcting end connecting rods 7 and the correcting end bearing plates 8 is the same as that of the first frames of the position correcting frames.
The shape of the correcting end follower block 6 is not particularly defined, and is, for example, a circle or a square.
The surface area of the correcting end conformal pressure block 6 is more than or equal to 30000mm 2 The thickness is more than or equal to 30 mm.
The diameter of the correcting end connecting rod 7 is more than or equal to 40 mm.
The length of the correcting end bearing plate 8 is more than or equal to 200mm, the width is more than or equal to 100mm, and the thickness is more than or equal to 60 mm.
According to the embodiment of the invention, the number of the correcting end limiting plates 9 is the same as that of the first frames of the correcting frames.
The correcting end limiting plate 9 is superposed with the center of the first frame of the correcting frame.
The material of the correcting end limiting plate 9 is medium carbon steel or stainless steel.
And a T-shaped groove structure is arranged in the correction end limiting plate 9.
The T-shaped groove structure is matched with the correction end connecting rod 7 and the correction end bearing plate 8.
The length of the correcting end limiting plate 9 is more than or equal to 300mm, the width is more than or equal to 160mm, and the thickness is more than or equal to 100 mm.
According to the embodiment of the invention, the material of the correcting end limiting plate connecting nut 10 and the correcting end limiting plate connecting screw rod 11 is medium carbon steel or stainless steel.
The circle centers of the correction end limiting plate connecting nut 10 and the correction end limiting plate connecting screw rod 11 are overlapped and have the same number.
Each correction end limiting plate 9 is in threaded connection with a correction end limiting plate connecting screw rod 11 through two correction end limiting plate connecting nuts 10.
According to the embodiment of the invention, the centers of the fixed end conformal pressing block 12, the fixed end limiting screw 17, the fixed end limiting screw stop plate 18 and the fixed end limiting screw stop plate stop nut 19 are overlapped and have the same number.
The fixed end conformal pressing block 12, the fixed end limiting screw 17, the fixed end limiting screw stop plate 18 and the fixed end limiting screw stop plate limiting nut 19 are made of low-carbon steel or die steel.
The shape of the fixed-end compact 12 is not particularly limited, and is, for example, circular or square.
The surface area of the fixed end conformal pressing block 12 is more than or equal to 20000mm 2 The thickness is more than or equal to 30 mm.
The diameter of the fixed end limiting screw 17 is more than or equal to 50mm, and the thread pitch is less than or equal to 1.0 mm.
The length of the fixed end limiting screw stop plate 18 is more than or equal to 60mm, the width is more than or equal to 40mm, and the thickness is more than or equal to 30 mm.
The thickness of the limiting nut 19 of the limiting plate of the fixed end limiting screw is more than or equal to 40mm, and the thread pitch is less than or equal to 1.0 mm.
The limiting nut 19 of the limiting plate of the fixed end limiting screw is in threaded connection with the limiting screw 17 of the fixed end, and the height of the limiting nut and the outer surface of the outer limiting block 16 of the fixed end after the limiting nut and the outer limiting screw are in threaded connection is lower than that of the outer limiting block of the fixed end.
According to the embodiment of the invention, the number of the fixed end inner limiting plates 13 is the same as that of the second frames of the positioning frame.
The fixed end inner limiting plate 13 is superposed with the center of the second frame of the position correcting frame.
The limiting plate 13 in the fixed end is made of low-carbon steel or stainless steel.
And the fixed end inner limit plate 13 is in contact with the fixed end limit screw rod 17.
The length of the limiting plate 13 in the fixed end is more than or equal to 200mm, the width is more than or equal to 120mm, and the thickness is more than or equal to 30 mm.
According to the embodiment of the invention, the circle centers of the fixed end inner limiting plate connecting nut 14 and the fixed end inner limiting plate connecting screw rod 15 are overlapped and have the same number.
Each fixed end inner limiting plate 13 is screwed with two fixed end inner limiting plate connecting nuts 14 and two fixed end inner limiting plate connecting screws 15.
The fixed end inner limiting plate connecting nut 14 and the fixed end inner limiting plate connecting screw rod 15 are made of medium carbon steel, die steel or stainless steel.
The diameter of the limiting plate connecting screw 15 in the fixed end is more than or equal to 30mm, and the length of the limiting plate connecting screw is less than or equal to 80 mm.
According to the embodiment of the present invention, the number of the fixed end outer stoppers 16 is the same as the number of the second frames of the calibration frame.
The outer limiting block 16 of the fixed end coincides with the center of the second frame of the position correcting frame.
The outer limiting block 16 of the fixed end is made of medium carbon steel or stainless steel.
A T-shaped groove structure is arranged in the fixed end outer limiting block 16.
The T-shaped groove structure is matched with the fixed end limit screw 17 and the fixed end limit screw stop plate 18.
The length of the fixed end outer limiting block 16 is more than or equal to 300mm, the width is more than or equal to 160mm, and the thickness is more than or equal to 100 mm.
According to the embodiment of the present invention, the fixed end outer limiting block fastening screw 20 and the fixed end outer limiting block fastening nut 21 are made of medium carbon steel or stainless steel.
The centers of circles of the fixed end outer limit block fastening screw rod 20 and the fixed end outer limit block fastening nut 21 are overlapped and are the same in quantity.
Each fixed end outer limiting block 16 is screwed with two fixed end outer limiting block fastening nuts 21 through two fixed end outer limiting block fastening screws 20, and the height after screwing is lower than the outer surface of the fixed end outer limiting block 16.
The diameter of the fixed end outer limiting block fastening screw rod 20 is less than or equal to 40mm, and the length of the fixed end outer limiting block fastening screw rod is less than or equal to 50 mm.
According to an embodiment of the invention, the device is placed on a hydraulic machine, preferably between a lower pressure table 27 and an upper pressure table 28 of the hydraulic machine.
According to an embodiment of the invention, the apparatus further comprises a shock motor 2, the shock motor 2 being located above the heat treatment support base 1.
The vibration exciting motor 2 is arranged for providing vibration for the aluminum alloy casting 23, so that the vibration aging stress eliminating treatment step can be conveniently completed.
According to the embodiment of the invention, the excitation motor 2 is positioned right above the heat treatment support base 1 and is overlapped with the center of the heat treatment support base 1.
The preparation method of the present invention will be described in further detail with reference to specific examples. It is to be understood that the following examples are only illustrative and explanatory of the present invention and should not be construed as limiting the scope of the present invention. All the technologies realized based on the above-mentioned contents of the present invention are covered in the protection scope of the present invention.
The experimental methods used in the following examples are all conventional methods unless otherwise specified; reagents, materials and the like used in the following examples are commercially available unless otherwise specified.
Example 1:
the preparation method of the high-strength and high-toughness aluminum alloy casting with vibration aging and cryogenic treatment low stress corrosion resistance is characterized by comprising the following preparation steps:
(1) secondary solid solution heat preservation treatment: placing the aluminum alloy casting in a solid solution heat preservation furnace for secondary solid solution heat preservation treatment;
(2) quenching heat treatment: placing the aluminum alloy casting subjected to the secondary solution heat-preservation heat treatment in a spray quenching furnace for spray quenching treatment, wherein spray heads symmetrically distributed along the aluminum alloy casting are installed in the spray quenching furnace, and the spray heads spray liquid quenching medium to carry out quenching heat treatment on the aluminum alloy casting;
(3) thermal state mechanical correction: adopting non-contact optical measurement equipment to perform size scanning analysis on the sprayed and quenched aluminum alloy casting, and then performing thermal state correction on the aluminum alloy casting by means of a mechanical correction device and a hydraulic device;
(4) pre-aging heat treatment: placing the aluminum alloy casting in an aging heat preservation furnace, and performing pre-aging heat preservation treatment;
(5) vibration aging treatment: after the pre-aging heat preservation heat treatment of the aluminum alloy casting is finished, taking the aluminum alloy casting out of the aging heat preservation furnace, carrying out vibration aging treatment on the aluminum alloy casting, and carrying out residual stress detection on the aluminum alloy casting before and after the vibration aging treatment;
(6) and (3) size stabilization treatment: placing the aluminum alloy casting subjected to the vibratory ageing treatment in a liquid nitrogen cold-state heat preservation furnace for size stabilization treatment;
(7) primary cryogenic treatment: after finishing size stabilization treatment, continuously placing the aluminum alloy casting in a liquid nitrogen cold-state heat preservation furnace for primary cryogenic treatment;
(8) aging heat treatment: placing the aluminum alloy casting subjected to primary subzero treatment in an aging heat treatment heat preservation furnace for aging heat treatment;
(9) secondary subzero treatment: and placing the aluminum alloy casting subjected to the aging heat treatment in a liquid nitrogen cold-state heat preservation furnace for secondary subzero treatment, and taking out the aluminum alloy casting after the secondary subzero treatment is finished, so as to finish the vibration aging and subzero treatment low-stress corrosion-resistant preparation of the high-strength and high-toughness aluminum alloy casting.
In the secondary solution heat-preservation heat treatment preparation step, the aluminum alloy casting is a ZL114A transition section metal shell casting; the charging temperature is 60 ℃, and the heating rate is 2 ℃ min -1 The temperature of the first-stage solid solution heat-preservation heat treatment is 540 ℃, the time of the first-stage solid solution heat-preservation heat treatment is 3 hours, the temperature of the second-stage solid solution heat-preservation heat treatment is 547 ℃, the time of the second-stage solid solution heat-preservation heat treatment is 12 hours, and T is Melting temperature of eutectic phase with low melting point The temperature is 550 ℃, and the temperature uniformity control range of the solid solution holding furnace is +/-2 ℃.
In the quenching heat treatment preparation step, the quenching transfer time is 4s, the spraying quenching medium is deionized water, and the spraying flow of a spray head is 0.20 L.s -1 The spraying time of the spray head is 5min, the spraying angle of the spray head ranges from minus 60 degrees to plus 60 degrees, and the diameter of a spray opening of the spray head is 1.0 mm.
In the thermal state mechanical correction preparation step, a detection light source of non-contact optical measurement equipment is laser, the number of single scanning points is 600 ten thousand, the point spacing is 0.018mm, and the measurement dimensional accuracy is +/-0.001 mm; the mechanical correction tool is of a steel structure, and the hydraulic pressure range of the hydraulic device is 2T.
In the preparation step of the pre-aging heat treatment, the charging temperature is 30 ℃, and the heating rate is 1.2 ℃ per minute -1 The preaging heat preservation temperature is 140 ℃, the preaging heat preservation time is 2 hours, and the furnace temperature uniformity temperature control range of the preaging heat preservation heat treatment furnace is +/-5 ℃.
In the vibration aging preparation step, an aluminum alloy casting residual stress detection device is X-ray residual stress detection equipment, a part to be detected of the aluminum alloy casting needs to be ground and polished before testing, grinding sand paper is 1000 meshes, polishing paste used during polishing is 3000 meshes, the measurement method is a tilting fixation method, radiation is Crk alpha, the X-ray pipeline voltage is 10kV, the X-ray pipeline current is 8mA, the single-point testing time is 0.5min, the 2 theta scanning starting angle is 160 degrees, and the 2 theta scanning ending angle is 120 degrees; the vibration aging excitation frequency is 180Hz, and the rotation speed of the excitation motor is 3500r.min -1 The vibration acceleration of the exciting motor is 30m.s -2 The exciting force is 800N, and the exciting time is 15 min.
In the preparation step of size stabilization treatment, the temperature of the size stabilization furnace is 20 ℃, and the cooling rate is-1.5 ℃ per minute -1 The temperature control range of the furnace temperature uniformity of the size stabilization treatment holding furnace is +/-5 ℃, the size stabilization holding temperature is-120 ℃, and the size stabilization holding time is 20 min.
In the preparation step of primary subzero treatment, the furnace temperature uniformity temperature control range of the holding furnace is +/-5 ℃, and the temperature reduction rate of the primary subzero treatment is-3.0 ℃ min -1 The temperature of the primary subzero treatment is-180 ℃, and the time of the primary subzero treatment is 40 min.
In the aging heat treatment preparation step, the charging temperature is room temperature, and the heating rate is 1.5 ℃ min -1 The temperature of the aging heat treatment is 160 ℃, the time of the aging heat treatment is 4 hours, and the temperature uniformity control range of the aging heat treatment holding furnace is +/-2 ℃.
In the preparation step of the secondary subzero treatment, the furnace temperature is 40 ℃, the furnace temperature uniformity temperature control range of the heat preservation furnace of the secondary subzero treatment is +/-5 ℃, and the temperature reduction rate of the secondary subzero treatment is-5.0 ℃ min -1 The heat preservation temperature of the secondary subzero treatment is-180 ℃, and the heat preservation time of the secondary subzero treatmentAnd (4) taking the casting out of the furnace and heating to room temperature after the secondary subzero treatment is finished for 20 min.
Example 2:
the preparation method of the aluminum alloy casting is the same as that of the example 1, and only differs from the following steps:
in the preparation step of the solution heat preservation treatment, the aluminum alloy casting is a ZL114A tail section metal shell casting; the solution heat-preservation heat treatment is a secondary solution heat preservation, the charging temperature is 50 ℃, and the heating rate is 2.5 ℃ per minute -1 The temperature of the first-stage solid solution heat preservation heat treatment is 540 ℃, the time of the first-stage solid solution heat preservation heat treatment is 4 hours, the temperature of the second-stage solid solution heat preservation heat treatment is 547 ℃, the time of the second-stage solid solution heat preservation heat treatment is 14 hours, T Melting temperature of eutectic phase with low melting point The temperature is 550 ℃, and the temperature uniformity control range of the solid solution holding furnace is +/-2 ℃.
In the quenching heat treatment preparation step, the quenching transfer time is 5s, the spraying quenching medium is deionized water, and the spraying flow of a spray head is 0.30 L.s -1 The spraying time of the spray head is 10min, the spraying angle of the spray head ranges from minus 40 degrees to plus 40 degrees, and the diameter of a spray opening of the spray head is 2.0 mm.
In the thermal state mechanical correction preparation step, a non-contact optical measurement device detects that a light source is laser, the number of single scanning points is 1200 ten thousand, the point spacing is 0.022mm, and the measurement size precision is +/-0.001 mm; the mechanical correcting device is of a steel structure, and the hydraulic pressure range of the hydraulic device is 4T.
In the preparation step of the pre-aging heat treatment, the charging temperature is 25 ℃, and the heating rate is 1.6 ℃ per minute -1 The preaging heat preservation temperature is 160 ℃, the preaging heat preservation time is 3h, and the furnace temperature uniformity temperature control range of the preaging heat preservation heat treatment furnace is +/-5 ℃.
In the vibration aging preparation step, an aluminum alloy casting residual stress detection device is X-ray residual stress detection equipment, a part to be detected of the aluminum alloy casting needs to be polished and polished before testing, polishing sand paper is 1200 meshes, polishing paste used during polishing is 4000 meshes, a measurement method is a tilting fixation method, radiation is Crk alpha, the voltage of an X-ray pipeline is 15kV, the current of the X-ray pipeline is 15mA, the single-point testing time is 1.0min, the 2 theta scanning initial angle is 150 degrees, and the 2 theta scanning final angle is 150 degreesThe stop angle is 120 degrees; the vibration aging excitation frequency is 240Hz, and the rotation speed of the excitation motor is 5000r.min -1 The vibration acceleration of the exciting motor is 60m.s -2 The exciting force is 1200N, and the exciting time is 25 min.
In the preparation step of size stabilization treatment, the temperature of the size stabilization furnace is 20 ℃, and the cooling rate is-1.4 ℃ per minute -1 The furnace temperature uniformity temperature control range of the size stabilization treatment holding furnace is +/-5 ℃, the size stabilization holding temperature is-115 ℃, and the size stabilization holding time is 30 min.
In the preparation step of the primary subzero treatment, the furnace temperature uniformity temperature control range of the holding furnace is +/-5 ℃, and the temperature reduction rate of the primary subzero treatment is-2.5 ℃ min -1 The temperature of the primary subzero treatment is-175 ℃, and the time of the primary subzero treatment is 50 min.
In the aging heat treatment preparation step, the charging temperature is room temperature, and the heating rate is 2.5 ℃ min -1 The temperature of the aging heat treatment is 170 ℃, the time of the aging heat treatment is 5 hours, and the temperature uniformity control range of the aging heat treatment holding furnace is +/-2 ℃.
In the preparation step of the secondary subzero treatment, the furnace temperature is 30 ℃, the furnace temperature uniformity temperature control range of the heat preservation furnace of the secondary subzero treatment is +/-5 ℃, and the temperature reduction rate of the secondary subzero treatment is-4.0 ℃ per minute -1 And the heat preservation temperature of the secondary subzero treatment is-170 ℃, the heat preservation time of the secondary subzero treatment is 25min, and the casting is taken out of the furnace and heated to the room temperature after the secondary subzero treatment is finished.
FIG. 3 shows the comparison of the residual stress of the ZL114A tail section metal shell casting of example 2 after the quenching heat treatment and the secondary cryogenic treatment. As can be seen from FIG. 3, after the secondary cryogenic treatment is carried out on the ZL114A tail section metal shell casting by adopting the preparation process of example 2, compared with the quenching heat treatment, the peak residual tensile stress is reduced from 234MPa to 84MPa, and is reduced by 64.1%; the peak residual compressive stress is reduced from-186 MPa to-76 MPa by 59.1 percent, and the residual stress in the casting is effectively reduced.
FIG. 4 shows the comparison result of the buckling size of the ZL114A tail section metal shell casting in example 2 after quenching heat treatment and secondary cryogenic treatment. As can be seen from FIG. 4, after the secondary deep cooling treatment is carried out on the ZL114A tail section metal shell casting by adopting the preparation process of example 2, the maximum positive warpage size is reduced from 5.4mm to 1.8mm, and is reduced by 66.6% compared with that after quenching heat treatment; the maximum negative warpage size is reduced from-4.6 mm to-1.4 mm, which is reduced by 69.6%, and the size deformation of the casting is effectively controlled.
The test results of fig. 3 and fig. 4 confirm that the residual stress and the dimensional deformation of the ZL114A tail section metal shell casting are effectively controlled after the preparation process of example 2, and the precision forming casting of the ZL114A tail section metal shell casting can be realized.
Example 3:
the preparation method of the aluminum alloy casting is the same as that of the embodiment 1, and only the following differences are included:
in the preparation step of the solution heat preservation treatment, the aluminum alloy casting is a ZL205A tail section metal shell casting; the solution heat-preservation heat treatment is a secondary solution heat preservation, the charging temperature is 50 ℃, and the heating rate is 3 ℃ per minute -1 The temperature of the first-stage solid solution heat preservation heat treatment is 545 ℃, the time of the first-stage solid solution heat preservation heat treatment is 5 hours, the temperature of the second-stage solid solution heat preservation heat treatment is 552 ℃, the time of the second-stage solid solution heat preservation heat treatment is 16 hours, T Melting temperature of eutectic phase with low melting point The temperature is 555 ℃, and the furnace temperature uniformity temperature control range of the solid solution holding furnace is +/-2 ℃.
In the quenching heat treatment preparation step, the quenching transfer time is less than or equal to 10s, the spray quenching medium is a polyethylene glycol organic quenching solvent, and the spray flow of a spray head is 0.45 L.s -1 The spraying time of the spray head is 15min, the spraying angle of the spray head is-30 to +30 degrees, and the diameter of a spray opening of the spray head is 3.0 mm.
In the thermal state mechanical correction preparation step, a detection light source of non-contact optical measurement equipment is laser, the number of single scanning points is 2000 ten thousand, the point spacing is 0.018mm, and the measurement size precision is +/-0.001 mm; the mechanical correcting device is of a steel structure, and the hydraulic pressure range of the hydraulic device is 5T.
In the preparation step of the pre-aging heat treatment, the charging temperature is 20 ℃, and the heating rate is 2.0 ℃ min -1 The preaging heat preservation temperature is 180 ℃, and the preaging heat preservation timeThe time is 4 hours, and the furnace temperature uniformity temperature control range of the pre-aging heat-preservation heat treatment furnace is +/-5 ℃.
In the vibration aging preparation step, an aluminum alloy casting residual stress detection device is an X-ray residual stress detection device, a part to be detected of the aluminum alloy casting needs to be polished before testing, polishing abrasive paper is 2000 meshes, polishing paste used during polishing is 6000 meshes, the measurement method is a tilting fixation method, a radiation line is Crk alpha, the voltage of an X-ray pipeline is 30kV, the current of the X-ray pipeline is 20mA, the single-point testing time is 1.2min, the 2 theta scanning starting angle is 140 degrees, and the 2 theta scanning ending angle is 110 degrees; the vibration aging excitation frequency is 320Hz, and the rotation speed of the excitation motor is 8000r.min -1 The vibration acceleration of the exciting motor is 80m.s -2 The exciting force is 2000N, and the exciting time is 30 min.
In the size stabilizing treatment preparation step, the temperature of the size stabilizing furnace is 20 ℃, and the cooling rate is-1.5 ℃ min -1 The temperature uniformity of the dimension stabilizing treatment holding furnace is controlled within the range of +/-5 ℃, the dimension stabilizing holding temperature is-110 ℃, and the dimension stabilizing holding time is 40 min.
In the preparation step of the primary subzero treatment, the furnace temperature uniformity temperature control range of the holding furnace is +/-5 ℃, and the temperature reduction rate of the primary subzero treatment is-3.0 ℃ min -1 The temperature of the primary subzero treatment is-180 ℃, and the time of the primary subzero treatment is 60 min.
In the aging heat treatment preparation step, the charging temperature is room temperature, and the heating rate is 3.0 ℃ min -1 The temperature of the aging heat treatment is 180 ℃, the time of the aging heat treatment is 6h, and the temperature uniformity control range of the aging heat treatment holding furnace is +/-2 ℃.
In the preparation step of the secondary subzero treatment, the furnace temperature is 25 ℃, the furnace temperature uniformity temperature control range of the heat preservation furnace of the secondary subzero treatment is +/-5 ℃, and the temperature reduction rate of the secondary subzero treatment is-5.0 ℃ min -1 And the heat preservation temperature of the secondary subzero treatment is-180 ℃, the heat preservation time of the secondary subzero treatment is 30min, and the casting is taken out of the furnace and heated to the room temperature after the secondary subzero treatment is finished.
FIG. 5 shows that the ZL205A tail section metal shell casting is heated by a traditional T6 heatThe treatment process compared the results of the post-preparation intra-crystalline and grain boundary TEM microstructure tests of example 3. As can be seen from the test results in FIG. 5, the in-crystal Al of the ZL205A end-section metal shell castings prepared in example 3 compared to the conventional T6 heat treatment process 2 The precipitation quantity of the Cu strengthening phase is greatly increased, the precipitation size is obviously refined, and the strength and the plastic toughness of the alloy material can be greatly improved; al of grain boundary region 2 The amount of Cu precipitated strengthening phases is obviously reduced, the width of a grain boundary precipitation-free zone PFZ is obviously increased, and the corrosion resistance of the alloy material can be effectively improved.
Comparative example 1:
the other operations are the same as example 1, except that the aluminum alloy casting is prepared by placing the stabilization preparation step before the pre-aging preparation step.
Comparative example 2:
the other operations are the same as those in the embodiment 2, and only the vibration aging treatment step is placed after the secondary deep cooling treatment in the preparation process of the aluminum alloy casting.
Comparative example 3:
the other operations are the same as those in the embodiment 3, and only the difference is that in the preparation process of the aluminum alloy casting, the preparation step of the pre-aging heat treatment is placed after the preparation step of the primary subzero treatment, and the preparation step of the aging heat treatment is placed after the preparation step of the secondary subzero treatment.
TABLE 1 results of comprehensive Properties test of castings prepared in examples 1 to 3 and comparative examples 1 to 3
Figure 908611DEST_PATH_IMAGE002
The embodiments of the present invention have been described above. However, the present invention is not limited to the above embodiment. Any modification, equivalent replacement, or improvement made within the spirit and principle of the present invention should be included in the protection scope of the present invention.

Claims (10)

1. A method for producing an aluminum alloy casting, characterized by comprising the steps of:
(1) placing the aluminum alloy casting in a solid solution heat preservation furnace for secondary solid solution heat preservation treatment;
(2) placing the aluminum alloy casting subjected to the secondary solution heat-preservation heat treatment in a spray quenching furnace for spray quenching treatment, wherein spray heads symmetrically distributed along the aluminum alloy casting are installed in the spray quenching furnace, and the spray heads spray liquid quenching medium to carry out quenching heat treatment on the aluminum alloy casting;
(3) scanning and analyzing the size of the sprayed and quenched aluminum alloy casting by adopting non-contact optical measuring equipment, and then carrying out thermal state correction on the aluminum alloy casting by using a mechanical correction device and a hydraulic device;
(4) placing the aluminum alloy casting in an aging heat preservation furnace, and performing pre-aging heat preservation treatment;
(5) after the pre-aging heat preservation heat treatment of the aluminum alloy casting is finished, taking the aluminum alloy casting out of the aging heat preservation furnace, and carrying out vibration aging treatment on the aluminum alloy casting;
(6) placing the aluminum alloy casting subjected to the vibratory ageing treatment in a liquid nitrogen cold-state heat preservation furnace for size stabilization treatment;
(7) after finishing size stabilization treatment, continuously placing the aluminum alloy casting in a liquid nitrogen cold-state heat preservation furnace for primary cryogenic treatment;
(8) placing the aluminum alloy casting subjected to primary subzero treatment in an aging heat treatment heat preservation furnace for aging heat treatment;
(9) and placing the aluminum alloy casting subjected to the aging heat treatment in a liquid nitrogen cold-state heat preservation furnace for secondary subzero treatment, and taking out the aluminum alloy casting after the secondary subzero treatment is finished, so as to finish the vibration aging and subzero treatment low-stress corrosion-resistant preparation of the high-strength and high-toughness aluminum alloy casting.
2. The production method according to claim 1, wherein in the step (1), the aluminum alloy casting is an aluminum-silicon-series aluminum alloy casting, an aluminum-copper-series aluminum alloy casting, or an aluminum-magnesium-series aluminum alloy casting;
and/or, in step (1), theThe temperature rise rate of the secondary solution heat-preservation treatment is 2 ℃ min -1 ~3℃·min -1 The secondary solution heat-preservation heat treatment comprises a primary solution heat-preservation heat treatment and a secondary solution heat-preservation heat treatment, wherein the temperature of the primary solution heat-preservation heat treatment is T Melting temperature of eutectic phase with low melting point The temperature is minus 10 ℃, the time of the first stage of solid solution heat preservation heat treatment is 3h to 5h, and the temperature of the second stage of solid solution heat preservation heat treatment is T Melting temperature of eutectic phase with low melting point And the time of the second-stage solid solution heat preservation heat treatment is 12-16 h at the temperature of minus 3 ℃.
3. The method according to claim 1, wherein in the step (2), the quenching transfer time is 10s or less;
and/or in the step (2), the sprayed quenching medium is deionized water or an organic quenching solvent such as polyethylene glycol, and the spraying flow of the spray header is 0.20 L.s -1 ~0.45L·s -1 The spraying time of the spray head is 5-15 min, the spraying angle of the spray head is-60 to +60 degrees, and the diameter of a spraying opening of the spray head is 1.0-3.0 mm.
4. The preparation method according to claim 1, wherein in the step (3), the detection light source of the non-contact optical measurement device is laser, the number of the single scanning points is 600 to 2000 ten thousand, the point spacing is 0.018 to 0.037mm, and the precision of the measurement size is ± 0.001 mm;
and/or in the step (3), the range of the hydraulic pressure provided by the hydraulic device is 1T-10T.
5. The production method according to claim 1, wherein in the step (4), the charging temperature of the aluminum alloy casting is less than 50 ℃;
and/or, in the step (4), the temperature rise rate of the pre-aging heat treatment is 1.2 ℃ min -1 ~2.0℃·min -1 The heat preservation temperature of the pre-aging heat treatment is 140-180 ℃, and the heat preservation time of the pre-aging heat treatment is 2-4 h.
6. The method of claim 1, wherein the method comprisesCharacterized in that in the step (5), the excitation frequency of the vibration aging heat treatment is 10 Hz-1000 Hz, and the rotation speed of the excitation motor is 1000r.min -1 ~10000r.min -1 The vibration acceleration of the exciting motor is 20m.s -2 ~100m.s -2 The exciting force is 500N-3000N, and the exciting time is 15 min-45 min.
7. The production method according to claim 1, wherein in the step (6), the charging temperature of the aluminum alloy casting is less than 40 ℃;
and/or, in step (6), the temperature reduction rate of the size stabilization treatment is-1.5 ℃ min -1 ~-1.2℃·min -1 The temperature for the size stabilizing treatment is-120 ℃ to-110 ℃, and the time for the size stabilizing treatment is 20min to 40 min.
8. The preparation method according to claim 1, wherein in the step (7), the temperature uniformity of the liquid nitrogen cold holding furnace is controlled within a range of +/-5 ℃;
and/or, in the step (7), the cooling rate of the primary cryogenic treatment is-3.0 ℃ min -1 ~-2.0℃·min -1 The heat preservation temperature of the primary subzero treatment is minus 180 ℃ to minus 170 ℃, and the heat preservation time of the primary subzero treatment is 40min to 60 min.
9. The preparation method of claim 1, wherein in the step (8), the charging temperature of the aluminum alloy casting is 20-40 ℃;
and/or, in the step (8), the temperature rise rate of the aging heat treatment is 1.5 ℃ min -1 ~3.0℃·min -1 The heat preservation temperature of the aging heat treatment is 160-180 ℃, and the heat preservation time of the aging heat treatment is 4-6 h.
10. The production method according to claim 1, wherein in the step (9), the temperature decrease rate of the secondary cryogenic treatment is-5.0 ℃. min -1 ~-3.0℃·min -1 The heat preservation temperature of the secondary subzero treatment is-180 ℃ to-160 ℃, and the heat preservation time of the secondary subzero treatment is20min~30min；
And/or in the step (9), discharging the aluminum alloy casting after the secondary cryogenic treatment is finished, and heating the aluminum alloy casting to room temperature.
CN202210659262.3A 2022-06-13 2022-06-13 Low-stress corrosion-resistant preparation method for aluminum alloy casting through vibratory aging and cryogenic treatment Active CN114737142B (en)

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