CN113106365A - Annealing method of 2219 aluminum alloy ingot and 2219 aluminum alloy deformation piece - Google Patents
Annealing method of 2219 aluminum alloy ingot and 2219 aluminum alloy deformation piece Download PDFInfo
- Publication number
- CN113106365A CN113106365A CN202110402254.6A CN202110402254A CN113106365A CN 113106365 A CN113106365 A CN 113106365A CN 202110402254 A CN202110402254 A CN 202110402254A CN 113106365 A CN113106365 A CN 113106365A
- Authority
- CN
- China
- Prior art keywords
- annealing
- aluminum alloy
- temperature
- ingot
- alloy ingot
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/057—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with copper as the next major constituent
Abstract
The invention discloses an annealing method of a 2219 aluminum alloy ingot and a 2219 aluminum alloy deformation piece, and belongs to the technical field of material heat treatment. The annealing method of the 2219 aluminum alloy ingot comprises the following steps: subjecting the 2219 aluminum alloy ingot to at least the following annealing operations: preserving heat for 4-6h under the conditions of 180-180 ℃ and 480 ℃, preserving heat for 8-12h under the conditions of 450-480 ℃ and preserving heat for 18-30h under the conditions of 515-535 ℃. By carrying out multistage homogenization heat treatment on the 2219 aluminum alloy ingot by the method, the internal stress of the ingot can be reduced, the microsegregation of alloy elements can be reduced, the shapes of reticular eutectic compounds and spheroidized coarse sharp second phases in the structure can be reduced, and the deformation processing performance of the 2219 aluminum alloy ingot and the service performance of a deformation piece can be improved.
Description
Technical Field
The invention relates to the technical field of material heat treatment, in particular to an annealing method of a 2219 aluminum alloy ingot and a 2219 aluminum alloy deformation piece.
Background
2219 aluminum alloy belongs to Al-Cu alloy, has higher strength and toughness, can keep stable performance for a long time in a lower temperature range to a higher temperature range, and has excellent processability, so the 2219 aluminum alloy has wide application in the field of aerospace, such as a storage tank of a rocket, and is applied in large quantity. In these fields, 2219 aluminum alloy deformation pieces are usually applied, i.e. 2219 aluminum alloy ingots are subjected to deformation processing before being put into use. As a basis for the deformation process, the quality of the ingot plays a crucial role in the properties of the final deformed part.
However, 2219 aluminum alloy ingot generally has the following problems: (1) in the semi-continuous casting process, the secondary water cooling strength is high, the heat of the core cannot be dissipated in time, and a large temperature gradient is formed between the edge part and the core part of the ingot, so that large internal stress exists in the ingot; (2)2219 aluminum alloy has high Cu content, and in addition, unbalanced solidification causes serious microsegregation of Cu element and a large amount of Al2Cu is gathered in a crystal boundary to form a netlike eutectic compound which is difficult to break; (3) the impurity elements such as Fe and Si are inevitably present in the ingot to form some coarse and sharp second phases such as Al5FeSi、Al8FeMg3Si6、Al8FeMg3Si5Etc., which tend to form stress concentrations during deformation processing. These problems weaken the processability of 2219 aluminum alloy, even lead to cracks and other defects in serious cases, and some problems still exist even after deformation processing, thus seriously restricting the final service performance of 2219 aluminum alloy deformation pieces. The severity of the above problem is exacerbated as the size of 2219 aluminum alloy ingots is increased.
In view of this, the invention is particularly proposed.
Disclosure of Invention
One of the objects of the present invention includes providing a method of annealing a 2219 aluminum alloy ingot to improve the above technical problems.
Another object of the present invention is to provide a 2219 aluminum alloy wrought product having a method of making the wrought product comprising the above annealing method.
The application can be realized as follows:
in a first aspect, the present application provides a method for annealing a 2219 aluminum alloy ingot, the method comprising the steps of annealing the 2219 aluminum alloy ingot by at least the following: preserving heat for 4-6h under the conditions of 180-180 ℃ and 480 ℃, preserving heat for 8-12h under the conditions of 450-480 ℃ and preserving heat for 18-30h under the conditions of 515-535 ℃.
In an alternative embodiment, the first ramp rate for the 2219 aluminum alloy ingot ramp to 180-240 ℃ is 40-60 ℃/h.
In an alternative embodiment, the second temperature-raising rate for raising the temperature from 180 ℃ to 240 ℃ to 450 ℃ to 480 ℃ is 90-120 ℃/h.
In an alternative embodiment, the third temperature increase rate from 450 ℃ to 480 ℃ to 515 ℃ to 535 ℃ is 90-120 ℃/h.
In an alternative embodiment, the 2219 aluminum alloy ingot has a diameter of 400-800 mm.
In an alternative embodiment, the 2219 aluminum alloy ingot has a diameter of 483-533mm and the annealing comprises: keeping the temperature for 4.5h at 200 ℃, keeping the temperature for 9.5h at 460 ℃, keeping the temperature for 100 ℃/h at 100 ℃/h, keeping the temperature for 24h at 525 ℃ and keeping the temperature for 100 ℃/h at 100 ℃/h.
In an alternative embodiment, the 2219 aluminum alloy ingot has a diameter of 711 and 762mm, and the annealing comprises: keeping the temperature for 5.5h at 220 ℃, keeping the temperature for 11h at 475 ℃, keeping the temperature for 27.5h at 530 ℃ and keeping the temperature for 115 ℃/h at a second temperature rise rate of 110 ℃/h.
In an alternative embodiment, the 2219 aluminum alloy ingot has a diameter of 400-432mm, and the annealing comprises: keeping the temperature at 185 ℃ for 4h, keeping the temperature at 455 ℃ for 8h, keeping the temperature at 520 ℃ for 18h, and keeping the temperature at 90 ℃/h for 95 ℃/h.
In an alternative embodiment, the annealing method further comprises cooling the annealed ingot.
In an alternative embodiment, the cooling mode is air cooling.
In a second aspect, the present application provides a 2219 aluminum alloy deformation, and a preparation method thereof comprises the annealing method provided by any one of the above embodiments.
The beneficial effect of this application includes:
the multi-stage uniform annealing method provided by the application can reduce the crack tendency of 2219 aluminum alloy ingot through reducing the internal stress of the ingot, and can reduce micro segregation, reduce reticular eutectic compounds and spheroidized coarse and sharp second phases through promoting the diffusion of alloy elements, thereby improving the deformation processing performance of the ingot, and improving the yield and the mechanical property of a deformed part.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings needed to be used in the embodiments will be briefly described below, it should be understood that the following drawings only illustrate some embodiments of the present invention and therefore should not be considered as limiting the scope, and for those skilled in the art, other related drawings can be obtained according to the drawings without inventive efforts.
FIG. 1 is a metallographic structure diagram of 2219 aluminum alloy ingots after annealing treatment in example 1 and comparative example 1;
FIG. 2 is a metallographic structure chart of 2219 aluminum alloy ingots after annealing treatment in example 2 and comparative example 2;
fig. 3 is a metallographic structure diagram of 2219 aluminum alloy ingots after annealing treatment in example 3 and comparative example 3.
Detailed Description
In order to make the objects, technical solutions and advantages of the embodiments of the present invention clearer, the technical solutions in the embodiments of the present invention will be clearly and completely described below. The examples, in which specific conditions are not specified, were conducted under conventional conditions or conditions recommended by the manufacturer. The reagents or instruments used are not indicated by the manufacturer, and are all conventional products available commercially.
The annealing method of a 2219 aluminum alloy ingot and a 2219 aluminum alloy deformed piece provided by the present application will be specifically described below.
Currently, in order to improve the quality of the ingot, the ingot is generally subjected to a homogenization annealing before the deformation process. In industrial production, a single-stage homogenization annealing process, i.e., a long-term incubation at a single, higher temperature, is most commonly employed.
However, the inventor indicates that: when the types of elements in the ingot are less, the types of intercrystalline second phases are single, and a better effect can be achieved by adopting single-stage homogenization annealing. However, when the number of element types in the ingot is large, the number of types of intergranular second phases becomes very complicated, and there may be a case where the low melting point phase and the high melting point phase are present at the same time. If a single-stage homogenizing annealing process is adopted, when the temperature is lower, although the low-melting-point phase can be ensured not to be over-sintered, the high-melting-point phase is difficult to be greatly dissolved into the matrix. When the temperature is higher, although solid solution of the high melting point phase into the matrix is facilitated, the risk of overburning of the low melting point phase is correspondingly increased. Once overburnt, the quality of the ingot will be greatly impaired.
2219 aluminum alloy contains high Cu content, Mn, V, Zr, Ti and impurities such as Mg, Fe, Si, Zn, etc., and the second phase component in the alloy is very complex (Al2Cu、Al5Cu2Mg8Si6、Al5FeSi、Al8FeMg3Si6、Al8FeMg3Si5、MgZn2、Al15Si2(FeMn)3AlCuMnFe, etc.), especially MgZn formed thereof2When the melting point of the primary phase is lower, the primary phase is easy to over-burn due to long-time heat preservation at the temperature of over 480 ℃, so that the single-stage homogenization annealing process is difficult to realize the reduction of the content of intercrystalline second phases and the spheroidization of coarse sharp second phase morphology on the premise of no over-burning.
In view of the above, the present application provides an annealing method suitable for 2219 aluminum alloy ingot, which adopts a multi-stage homogenization annealing manner, and specifically includes the following steps: subjecting the 2219 aluminum alloy ingot to at least the following annealing operations: preserving heat for 4-6h under the conditions of 180-180 ℃ and 480 ℃, preserving heat for 8-12h under the conditions of 450-480 ℃ and preserving heat for 18-30h under the conditions of 515-535 ℃.
It should be noted that the above-mentioned heat preservation at 180-240 ℃ for 4-6h can be regarded as the 1 st annealing, the heat preservation at 450-480 ℃ for 8-12h can be regarded as the 2 nd annealing, and the heat preservation at 515-535 ℃ for 18-30h can be regarded as the 3 rd annealing. In some embodiments, it is not excluded to add further annealing operations before or after the 3 annealing operations (and each annealing operation) described above.
The temperature of the first annealing may be 180 ℃, 190 ℃, 200 ℃, 210 ℃, 220 ℃, 230 ℃ or 240 ℃, 185 ℃, 195 ℃, 205 ℃, 215 ℃ or 225 ℃, or any other temperature within the range of 180 ℃ to 240 ℃.
The heat preservation time of the 1 st annealing can be 4h, 4.5h, 5h, 5.5h or 6h, and can also be any other time value within the range of 4-6 h.
The temperature of the 2 nd annealing can be 450 ℃, 460 ℃, 470 ℃ or 480 ℃, etc., can also be 455 ℃, 465 ℃ or 475 ℃, etc., and can also be any other temperature value within the range of 450-.
The heat preservation time of the 2 nd annealing can be 8h, 9h, 10h, 11h or 12h, and can also be any other time value within the range of 8-12 h.
The heat preservation time of the 3 rd annealing can be 515 ℃, 525 ℃ or 535 ℃, can also be 520 ℃ or 530 ℃, and can also be any other time value within the range of 515 ℃ and 535 ℃.
The heat preservation time of the 3 rd annealing can be 18h, 20h, 22h, 25h, 28h or 30h, and the like, and can also be any other time value within the range of 18-30 h.
In alternative embodiments, the first ramp rate of the 2219 aluminum alloy ingot ramp to the 1 st annealing temperature may be 40-60 ℃/h, such as 40 ℃/h, 45 ℃/h, 50 ℃/h, 55 ℃/h, or 60 ℃/h.
It is worth to say that in the application, the first heating rate is set to be 40-60 ℃/h, and the 1 st annealing is set to be heat preservation for 4-6h at the temperature of 180-240 ℃, so that the 2219 aluminum alloy can be slowly heated to a lower temperature, internal stress can be gradually released, and the crack tendency can be further reduced. In the process, if the temperature of the 1 st annealing is lower than 180 ℃ and the holding time is shorter than 4h, incomplete internal stress release is easily caused, and if the temperature is higher than 240 ℃ and longer than 6h, excessive energy consumption after the internal stress is eliminated is easily caused.
In alternative embodiments, the second ramp rate for ramping the 1 st anneal temperature to the 2 nd anneal temperature is from 90 ℃/h to 120 ℃/h, such as 90 ℃/h, 95 ℃/h, 100 ℃/h, 105 ℃/h, 110 ℃/h, 115 ℃/h, or 120 ℃/h.
It is worth to be noted that, in the present application, the second temperature-raising rate is set to 90-120 ℃/h and the 2 nd annealing is set to heat preservation at 480 ℃ of 450-. In this process, if the temperature of the 2 nd annealing is lower than 450 ℃ and shorter than 8 hours, the second phase is liable to be incompletely dissolved and remains in the grain boundary in a large amount, and if it is higher than 480 ℃ and longer than 12 hours, the low-melting second phase is liable to be excessively sintered.
In alternative embodiments, the third ramp rate for ramping the 2 nd anneal temperature to the 3 rd anneal temperature is from 90 ℃/h to 120 ℃/h, such as 90 ℃/h, 95 ℃/h, 100 ℃/h, 105 ℃/h, 110 ℃/h, 115 ℃/h, or 120 ℃/h.
It is worth noting that in the present application, the third temperature-raising rate is set to 90-120 ℃/h and the 3 rd annealing is set to heat preservation at 515-. In the process, if the temperature of the 3 rd annealing is lower than 515 ℃ and shorter than 18h, the solid solution of the second phase with higher melting point is incomplete and the spheroidization degree of the coarse sharp second phase morphology is limited, and is higher than 535 ℃ and longer than 30h, the second phase with higher melting point is easy to be over-burnt, and the spheroidization degree of the coarse sharp second phase morphology reaches the maximum, so that the energy consumption is increased greatly in the prolonged time.
In an alternative embodiment, the 2219 aluminum alloy ingot has a diameter of 400-800mm, and 2219 aluminum alloy ingots within this diameter range are particularly suitable for the annealing process of the present application.
In some embodiments, the 2219 aluminum alloy ingot has a diameter of 483-533mm, the 1 st anneal is performed at 200 ℃ for 4.5 hours, the first ramp-up rate is 50 ℃/h, the 2 nd anneal is performed at 460 ℃ for 9.5 hours, the second ramp-up rate is 100 ℃/h, the 3 rd anneal is performed at 525 ℃ for 24 hours, and the third ramp-up rate is 100 ℃/h.
In other embodiments, the 2219 aluminum alloy ingot has a diameter of 711-.
In other embodiments, the 2219 aluminum alloy ingot has a diameter of 400-432mm, the 1 st anneal is performed at 185 ℃ for 4h, the first temperature rise rate is 60 ℃/h, the 2 nd anneal is performed at 455 ℃ for 8h, the second temperature rise rate is 90 ℃/h, the 3 rd anneal is performed at 520 ℃ for 18h, and the third temperature rise rate is 95 ℃/h.
Further, after the 3 rd annealing treatment, the obtained ingot was cooled.
In an alternative embodiment, the cooling mode is air cooling. And specifically, cooling the mixture to room temperature in air.
In summary, the annealing method provided by the application reduces the crack tendency by reducing the internal stress of the ingot, reduces the microsegregation by promoting the diffusion of alloy elements, reduces the reticular eutectic compound and spheroidized coarse and sharp second phases, further improves the deformation processing performance of the ingot, and improves the yield and the mechanical properties of a deformed part (such as the tensile strength, the yield strength and the elongation of the annealed ingot).
In addition, the application also provides a 2219 aluminum alloy deformation piece, and the preparation method comprises the annealing method, for example, the ingot after the annealing treatment can be subjected to deformation processing. It should be noted that the present application does not limit the specific process of the deformation process too much, and can refer to the prior art directly. The 2219 aluminum alloy deformation piece has good performances such as tensile strength, yield strength and elongation.
The features and properties of the present invention are described in further detail below with reference to examples.
Example 1
The embodiment provides a multistage homogenizing annealing method for a 2219 aluminum alloy ingot with the diameter of 508mm, which comprises the following steps:
(1) annealing for the 1 st time: heating a 2219 aluminum alloy cast ingot to 200 ℃ in a heat treatment furnace at a first heating rate of 50 ℃/h, and preserving heat for 4.5 h;
(2) and 2, annealing for the second time: heating the ingot subjected to the 1 st annealing treatment to 460 ℃ at a second heating rate of 100 ℃/h, and preserving heat for 9.5 h;
(3) annealing for the 3 rd time: heating the cast ingot subjected to the 2 nd annealing treatment to 525 ℃ at a third heating rate of 100 ℃/h, and preserving heat for 24 h;
(4) and (3) cooling: and cooling the ingot subjected to the 3 rd annealing treatment to room temperature in air.
Comparative example 1
Taking example 1 as an example, comparative example 1 was set, and comparative example 1 was divided into a treatment group a and a treatment group B.
The treatment group A is to carry out single-stage homogenizing annealing on 2219 aluminum alloy ingots with the diameter of 508mm, which are the same as that of the batch of the ingot in the example 1, and specifically comprises the following steps: directly keeping the cast ingot at 460 ℃ for 38 h.
The B treatment group also carries out single-stage homogenizing annealing on 2219 aluminum alloy ingots with the diameter of 508mm, which are the same as that of the example 1, and specifically comprises the following steps: directly keeping the cast ingot at 525 ℃ for 24 h.
The 2219 aluminum alloy ingots obtained after annealing treatment in example 1 and comparative example 1 were subjected to structure observation, and the results are shown in fig. 1.
FIG. 1(a) is a metallographic structure diagram of a 508mm 2219 aluminum alloy ingot with a diameter subjected to the multistage homogenization annealing treatment in example 1, FIG. 1(B) is a metallographic structure diagram of a 508mm 2219 aluminum alloy ingot with a diameter subjected to the single-stage homogenization annealing treatment of 460 ℃ heat preservation for 38h in treatment group A, and FIG. 1(c) is a metallographic structure diagram of a 508mm 2219 aluminum alloy ingot with a diameter subjected to the single-stage homogenization annealing treatment of 525 ℃ heat preservation for 24h in treatment group B.
As can be seen from fig. 1: after the multi-stage homogenizing annealing treatment provided by the embodiment 1, the size of the second phase at the grain boundary is small, the reticular eutectic compound disappears, and the overburning phenomenon does not appear. After the single-stage homogenization annealing treatment of 460 ℃ heat preservation for 38 hours provided by the treatment group A, the size and the number of second phases at the crystal boundary are larger, the appearance of some phases is sharper, and a reticular eutectic compound still exists; after the single-stage homogenizing annealing treatment of the treatment group B for heat preservation at 525 ℃ for 24 hours, the size of the second phase at the grain boundary is large, and the overburning phenomenon occurs.
Example 2
The embodiment provides a multistage homogenizing annealing method for a 2219 aluminum alloy ingot with the diameter of 730mm, which comprises the following steps:
(1) annealing for the 1 st time: heating a 2219 aluminum alloy cast ingot to 220 ℃ in a heat treatment furnace at a first heating rate of 40 ℃/h, and preserving heat for 5.5 h;
(2) and 2, annealing for the second time: heating the ingot subjected to the 1 st annealing treatment to 475 ℃ at a second heating rate of 110 ℃/h, and preserving heat for 11 h;
(3) annealing for the 3 rd time: heating the cast ingot subjected to the 2 nd annealing treatment to 530 ℃ at a third heating rate of 115 ℃/h, and preserving heat for 27.5 h;
(4) and (3) cooling: and cooling the ingot subjected to the 3 rd annealing treatment to room temperature in air.
Comparative example 2
Taking example 2 as an example, comparative example 2 was set, and comparative example 2 was divided into treatment group C and treatment group D.
The treatment group C is to carry out single-stage homogenizing annealing on 2219 aluminum alloy ingots with the diameter of 730mm, which are the same as that of the batch of the 2219 aluminum alloy ingots in the example 2, and specifically comprises the following steps: the ingot was directly kept at 475 ℃ for 46 h.
The treatment group D also carries out single-stage homogenizing annealing on 2219 aluminum alloy ingots with the diameter of 730mm, which are the same as that of the batch of the 2219 aluminum alloy ingots in the example 2, and specifically comprises the following steps: directly keeping the cast ingot at 530 ℃ for 26 h.
The 2219 aluminum alloy ingots obtained after annealing treatment in example 2 and comparative example 2 were subjected to structure observation, and the results are shown in fig. 2.
FIG. 2(a) is a metallographic structure of a 730mm 2219 aluminum alloy ingot with a diameter subjected to the multistage homogenization annealing treatment in example 2, FIG. 2(b) is a metallographic structure of a 730mm 2219 aluminum alloy ingot with a diameter subjected to the single-stage homogenization annealing treatment at 475 ℃ for 46h in the treatment group C, and FIG. 2(C) is a metallographic structure of a 730mm 2219 aluminum alloy ingot with a diameter subjected to the single-stage homogenization annealing treatment at 530 ℃ for 26h in the treatment group D.
As can be seen from fig. 2: after the multi-stage homogenizing annealing treatment provided in example 2, the coarse second phase had been completely solutionized into the matrix. After single-stage homogenizing annealing treatment of 475 ℃ heat preservation for 46h provided by the treatment group C, a small amount of second phases with thicker sizes still exist in the grain boundary, and part of the second phases have sharper appearances. After single-stage homogenizing annealing treatment of 530 ℃ heat preservation for 26h provided by the treatment group D, the second phase at the grain boundary is over-sintered.
Example 3
The embodiment provides a multistage homogenizing annealing method for a 2219 aluminum alloy ingot with the diameter of 420mm, which comprises the following steps:
(1) annealing for the 1 st time: heating a 2219 aluminum alloy cast ingot to 185 ℃ in a heat treatment furnace at a first heating rate of 60 ℃/h, and preserving heat for 4 h;
(2) and 2, annealing for the second time: heating the ingot subjected to the 1 st annealing treatment to 455 ℃ at a second heating rate of 90 ℃/h, and preserving heat for 8 h;
(3) annealing for the 3 rd time: heating the cast ingot subjected to the 2 nd annealing treatment to 520 ℃ at a third heating rate of 95 ℃/h, and preserving heat for 18 h;
(4) and (3) cooling: and cooling the ingot subjected to the 3 rd annealing treatment to room temperature in air.
Comparative example 3
Taking example 3 as an example, comparative example 3, i.e., the E-treatment group, was set.
The E treatment group is to carry out single-stage homogenizing annealing on 2219 aluminum alloy ingots with the same batch and the diameter of 420mm as that of the example 3, and specifically comprises the following steps: directly keeping the cast ingot at 515 ℃ for 32 h.
The 2219 aluminum alloy ingots obtained after the annealing treatment in example 3 and comparative example 3 were subjected to cogging forging and T6 heat treatment to be deformed into ring members, which were designated as deformed member 1 and deformed member 2.
The specific processing flow is as follows: blanking → rounding at two ends → heating 460 ℃ → pressing cake to 150mm high by an oil press → punching Φ 180mm → heating 460 ℃ → reaming by a single-arm hammer to Φ 550mm → leveling by a 2T hammer to 140mm high → heating 460 ℃ → looping by a 3m numerical control looping machine to 80mm of wall thickness.
T6 heat treatment schedule: solution treatment at 525 ℃ for 6.5h → quenching (water temperature not more than 30 ℃) → 170 ℃ for 18 h.
The resulting deformed element is shown in an organized view in fig. 3.
FIG. 3(a) is a metallographic representation of a 2219 aluminum alloy ingot with a diameter of 420mm after cogging and heat treatment of T6 after the multistage homogenization annealing treatment in example 3, and FIG. 3(b) is a metallographic representation of a 2219 aluminum alloy ingot with a diameter of 420mm after cogging and heat treatment of T6 after single-stage homogenization annealing at 515 ℃ for 32h in the E treatment group.
As can be seen from fig. 3: the ingot after the multi-stage homogenizing annealing treatment provided by the embodiment 3 has the deformation member (deformation member 1) with smaller size and more uniform dispersion of the second phase. For the ingot after the single-stage homogenizing annealing treatment provided by the treatment group E, the size of the second phase in the deformation piece (deformation piece 2) is larger, the agglomeration phenomenon exists at the grain boundary, and the reticular eutectic compound still exists.
Samples are respectively selected in the axial direction, the radial direction and the tangential direction of the deformation piece 1 and the deformation piece 2, and mechanical property tests are carried out on the samples, wherein the test standards of the tensile strength, the yield strength and the elongation rate refer to samples and methods for a tensile test of GB/T16865-.
TABLE 1 axial mechanical Properties
TABLE 2 radial mechanical Properties
TABLE 3 tangential mechanical Properties
As can be seen from table 1: in the axial direction, the tensile strength, the yield strength and the elongation of the multi-stage homogenizing annealing cast ingot are respectively 12 percent, 13 percent and 100 percent higher than those of the single-stage homogenizing annealing cast ingot.
As can be seen from table 2: in the radial direction, the tensile strength, the yield strength and the elongation of the multi-stage homogenizing annealing cast ingot are respectively 10 percent, 12 percent and 100 percent higher than those of the single-stage homogenizing annealing cast ingot.
As can be seen from table 3: in the tangential direction, the tensile strength, the yield strength and the elongation of the multi-stage homogenizing annealing cast ingot are respectively 13 percent, 12 percent and 133 percent higher than those of the single-stage homogenizing annealing cast ingot.
Compared with single-stage homogenization annealing, the mechanical property of the ingot subjected to multi-stage homogenization annealing after deformation processing is higher.
Comparative example 4
Taking example 1 as an example, comparative example 4 was set, and comparative example 4 was divided into H1-treated group to L3-treated group.
The H1 treatment group differed from example 1 in that: the 2 nd annealing is carried out at 400 ℃ for 9.5h, the second heating rate is 100 ℃/h, and the rest of the process is the same as that of the example 1.
The H2 treatment group differed from example 1 in that: the 2 nd annealing is carried out at 500 ℃ for 9.5h, the second heating rate is 100 ℃/h, and the rest of the process is the same as that of the example 1.
The I1 treatment group differed from example 1 in that: the 2 nd annealing is carried out at 460 ℃ for 6h, the second heating rate is 100 ℃/h, and the rest of the process is the same as that of the example 1.
The I2 treatment group differed from example 1 in that: the 2 nd annealing is carried out at 460 ℃ for 15h, the second heating rate is 100 ℃/h, and the rest of the process is the same as that of the example 1.
The J1 treatment group differed from example 1 in that: the 3 rd annealing is carried out for 24h under the condition of 500 ℃, the third heating rate is 100 ℃/h, and the rest processes are the same as the example 1.
The J2 treatment group differed from example 1 in that: the 3 rd annealing is carried out for 24h at 550 ℃, the third heating rate is 100 ℃/h, and the rest of the process is the same as that of the example 1.
The K1 treatment group differed from example 1 in that: the annealing of the 3 rd time is kept at 525 ℃ for 15h, the third heating rate is 100 ℃/h, and the rest processes are the same as the example 1.
The K2 treatment group differed from example 1 in that: the annealing of the 3 rd time is kept at 525 ℃ for 35h, the third heating rate is 100 ℃/h, and the rest processes are the same as the example 1.
The L1 treatment group differed from example 1 in that: the L1 treated group underwent only two anneals, not three. Annealing protocol for the L1 treatment group: the 1 st annealing is carried out for 4.5h under the condition of 200 ℃, and the first heating rate is 50 ℃/h; the 2 nd annealing is carried out for 9.5h under the condition of 460 ℃, and the second temperature rise rate is 100 ℃/h.
The L2 treatment group differed from example 1 in that: the L2 treated group underwent only two anneals, not three. Annealing protocol for the L2 treatment group: the 1 st annealing is carried out for 9.5h under the condition of 460 ℃, and the first heating rate is 100 ℃/h; the 2 nd annealing is carried out for 24h under the condition of 525 ℃, and the second temperature rise rate is 100 ℃/h.
The L3 treatment group differed from example 1 in that: the L3 treated group underwent only two anneals, not three. Annealing protocol for the L3 treatment group: the 1 st annealing is carried out for 4.5h under the condition of 200 ℃, and the first heating rate is 100 ℃/h; the 2 nd annealing is carried out for 24h under the condition of 525 ℃, and the second temperature rise rate is 100 ℃/h.
Comparative example results:
h1: the annealing temperature of the 2 nd time is lower, the solid solution of the second phase with low melting point is not thorough, and more residues are left, so the low melting point phase is over-burnt after the 3 rd time annealing.
H2: the higher temperature of the 2 nd annealing results in the low melting second phase being over-fired after the 2 nd annealing.
I1: the annealing time of the 2 nd time is short, the low-melting-point second phase is not completely dissolved, and more residues are left, so that the low-melting-point phase is over-burnt after the 3 rd annealing.
I2: the time of the 2 nd annealing is too long, so that the low-melting-point second phase is over-burnt after the 2 nd annealing, and the energy consumption is too large.
J1: the 3 rd annealing temperature is low, the second phase with higher melting point is not dissolved thoroughly, the grain boundary is remained, and the appearance of the sharp and thick second phase has no obvious spheroidization phenomenon.
J2: the 3 rd anneal temperature is too high (above the solidus) resulting in severe overburning of the second phase and the substrate.
K1: the 3 rd annealing time is short, so that the second phase with higher melting point is not dissolved completely, and the spheroidization degree of the coarse and sharp second phase is poor.
K2: the 3 rd annealing time is too long, so that the second phase with higher melting point is over-sintered and the energy consumption is too large.
L1: the second phase with higher melting point is remained in the grain boundary in a large quantity, and has more coarse and sharp second phases and no obvious spheroidization in appearance.
L2: the internal stress in the ingot is not released slowly, and crack defects appear in the forging process with large deformation.
L3: the low melting phase is severely over-fired and the coarse sharp second phase is less spheroidized.
Example 4
The present example provides a multistage homogenizing annealing method for 2219 aluminum alloy ingot with a diameter of 508mm, which is different from example 1 in that: the first temperature rise rate is 45 ℃/h, the first annealing temperature is 210 ℃ and the time is 4h, the second annealing temperature is 470 ℃ and the time is 8h, and the rest of the process is the same as that of the example 1.
Example 5
The present example provides a multistage homogenizing annealing method for 2219 aluminum alloy ingot with a diameter of 508mm, which is different from example 1 in that: the third annealing temperature is 530 ℃ and the time is 21.5h, and the rest processes are the same as the example 1.
Example 6
The present example provides a multistage homogenizing annealing method for 2219 aluminum alloy ingot with a diameter of 508mm, which is different from example 1 in that: the second heating rate is 120 ℃/h, the second annealing temperature is 480 ℃, the time is 8h, and the rest of the process is the same as that of the example 1.
The 2219 aluminum alloy ingots treated in examples 4, 5 and 6 had a smaller number of higher melting point phases at grain boundaries and smaller size than the 2219 aluminum alloy ingot treated in example 1, with a comparable degree of spheroidization of sharp and coarse second phase morphology. In the extrusion and forging processes, no defects such as cracks and the like appear, and the mechanical properties of the deformation pieces are similar.
In summary, the annealing method provided by the application reduces the crack tendency by reducing the internal stress of the ingot, reduces the microsegregation by promoting the diffusion of the alloy elements, reduces the reticular eutectic compound and the spheroidization of the coarse and sharp second phase, and further improves the deformation processing performance of the ingot, the yield and the mechanical property of the deformed part.
The above is only a preferred embodiment of the present invention, and is not intended to limit the present invention, and various modifications and changes will occur to those skilled in the art. 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. The annealing method of the 2219 aluminum alloy ingot is characterized by comprising the following steps of: subjecting the 2219 aluminum alloy ingot to at least the following annealing operations: preserving heat for 4-6h under the conditions of 180-180 ℃ and 480 ℃, preserving heat for 8-12h under the conditions of 450-480 ℃ and preserving heat for 18-30h under the conditions of 515-535 ℃.
2. The annealing method as claimed in claim 1, wherein the first temperature-rise rate for raising the temperature of the 2219 aluminum alloy ingot to 180-240 ℃ is 40-60 ℃/h.
3. The annealing method according to claim 2, wherein the second temperature-raising rate for raising the temperature from 180 ℃ to 240 ℃ to 450 ℃ to 480 ℃ is 90-120 ℃/h.
4. The annealing method according to claim 3, wherein the third temperature-raising rate from 450-480 ℃ to 515-535 ℃ is 90-120 ℃/h.
5. The annealing method according to any one of claims 1 to 4, wherein the 2219 aluminum alloy ingot has a diameter of 400-800 mm.
6. The annealing method of claim 5, wherein the 2219 aluminum alloy ingot has a diameter of 483-533mm, and the annealing comprises: keeping the temperature for 4.5h at 200 ℃, keeping the temperature for 9.5h at 460 ℃, keeping the temperature for 100 ℃/h at 100 ℃/h, keeping the temperature for 24h at 525 ℃ and keeping the temperature for 100 ℃/h at 100 ℃/h.
7. The annealing method as claimed in claim 5, wherein the 2219 aluminum alloy ingot has a diameter of 711 and 762mm, and the annealing comprises: keeping the temperature for 5.5h at 220 ℃, keeping the temperature for 11h at 475 ℃, keeping the temperature for 27.5h at 530 ℃ and keeping the temperature for 115 ℃/h at a second temperature rise rate of 110 ℃/h.
8. The annealing method as claimed in claim 5, wherein the 2219 aluminum alloy ingot has a diameter of 400-432mm, and the annealing comprises: keeping the temperature at 185 ℃ for 4h, keeping the temperature at 455 ℃ for 8h, keeping the temperature at 520 ℃ for 18h, and keeping the temperature at 90 ℃/h for 95 ℃/h.
9. The annealing method according to any one of claims 1 to 4, further comprising cooling the annealed ingot.
10. A 2219 aluminum alloy deformation characterized in that the method of making the 2219 aluminum alloy deformation comprises the annealing method of any of claims 1-9.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202110402254.6A CN113106365B (en) | 2021-04-14 | 2021-04-14 | Annealing method of 2219 aluminum alloy ingot and 2219 aluminum alloy deformation piece |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202110402254.6A CN113106365B (en) | 2021-04-14 | 2021-04-14 | Annealing method of 2219 aluminum alloy ingot and 2219 aluminum alloy deformation piece |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN113106365A true CN113106365A (en) | 2021-07-13 |
| CN113106365B CN113106365B (en) | 2021-12-28 |
Family
ID=76717177
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202110402254.6A Active CN113106365B (en) | 2021-04-14 | 2021-04-14 | Annealing method of 2219 aluminum alloy ingot and 2219 aluminum alloy deformation piece |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN113106365B (en) |
Citations (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4897124A (en) * | 1987-07-02 | 1990-01-30 | Sky Aluminium Co., Ltd. | Aluminum-alloy rolled sheet for forming and production method therefor |
| US5582659A (en) * | 1993-10-12 | 1996-12-10 | Nippon Light Metal Co., Ltd. | Aluminum alloy for forging, process for casting the same and process for heat treating the same |
| CN104762574A (en) * | 2015-03-29 | 2015-07-08 | 北京工业大学 | Homogenizing treatment method of Al-Zn-Mg alloy semi-continuous casting round ingot for high-speed rails |
| CN104805385A (en) * | 2015-05-07 | 2015-07-29 | 广西南南铝加工有限公司 | Homogenization thermal-treatment method for ultra-large semi-continuous cast round ingot |
| CN106399883A (en) * | 2016-10-31 | 2017-02-15 | 中南大学 | Homogenizing heat treatment technology for eliminating Al-Cu-Mg-Si-Mn alloy casting crystal phase |
| CN106834986A (en) * | 2017-03-07 | 2017-06-13 | 烟台南山学院 | A kind of aviation alloyed aluminium homogenizing heat treatment |
| CN110423927A (en) * | 2019-07-17 | 2019-11-08 | 中南大学 | A kind of Ultrahigh strength aluminum lithium alloy and preparation method thereof |
| CN110592448A (en) * | 2019-08-27 | 2019-12-20 | 江苏大学 | Novel heat-resistant corrosion-resistant 2219 type aluminum alloy and preparation method thereof |
| CN110714174A (en) * | 2019-09-23 | 2020-01-21 | 四川阳光坚端铝业有限公司 | Homogenization treatment process of aluminum alloy ingot |
| CN110923528A (en) * | 2019-11-27 | 2020-03-27 | 新疆众和股份有限公司 | Anode aluminum foil and manufacturing method thereof |
-
2021
- 2021-04-14 CN CN202110402254.6A patent/CN113106365B/en active Active
Patent Citations (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4897124A (en) * | 1987-07-02 | 1990-01-30 | Sky Aluminium Co., Ltd. | Aluminum-alloy rolled sheet for forming and production method therefor |
| US5582659A (en) * | 1993-10-12 | 1996-12-10 | Nippon Light Metal Co., Ltd. | Aluminum alloy for forging, process for casting the same and process for heat treating the same |
| CN104762574A (en) * | 2015-03-29 | 2015-07-08 | 北京工业大学 | Homogenizing treatment method of Al-Zn-Mg alloy semi-continuous casting round ingot for high-speed rails |
| CN104805385A (en) * | 2015-05-07 | 2015-07-29 | 广西南南铝加工有限公司 | Homogenization thermal-treatment method for ultra-large semi-continuous cast round ingot |
| CN106399883A (en) * | 2016-10-31 | 2017-02-15 | 中南大学 | Homogenizing heat treatment technology for eliminating Al-Cu-Mg-Si-Mn alloy casting crystal phase |
| CN106834986A (en) * | 2017-03-07 | 2017-06-13 | 烟台南山学院 | A kind of aviation alloyed aluminium homogenizing heat treatment |
| CN110423927A (en) * | 2019-07-17 | 2019-11-08 | 中南大学 | A kind of Ultrahigh strength aluminum lithium alloy and preparation method thereof |
| CN110592448A (en) * | 2019-08-27 | 2019-12-20 | 江苏大学 | Novel heat-resistant corrosion-resistant 2219 type aluminum alloy and preparation method thereof |
| CN110714174A (en) * | 2019-09-23 | 2020-01-21 | 四川阳光坚端铝业有限公司 | Homogenization treatment process of aluminum alloy ingot |
| CN110923528A (en) * | 2019-11-27 | 2020-03-27 | 新疆众和股份有限公司 | Anode aluminum foil and manufacturing method thereof |
Non-Patent Citations (1)
| Title |
|---|
| 阳代军等: ""2219铝合金大直径圆锭铸造性能分析及其改进措施"", 《航天制造技术》 * |
Also Published As
| Publication number | Publication date |
|---|---|
| CN113106365B (en) | 2021-12-28 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN109439976B (en) | Composite modification method for casting aluminum-silicon alloy | |
| CN111485132B (en) | Copper alloy strip with excellent comprehensive performance and preparation method thereof | |
| CN113234949B (en) | Method for preparing regenerated wrought aluminum alloy from waste aluminum alloy | |
| CN112941377A (en) | Er-containing cast heat-resistant Al-Si-Cu-Mg alloy | |
| CN111218590A (en) | High-strength high-formability aluminum-magnesium-copper alloy plate and preparation method thereof | |
| CN110983118B (en) | Production process of aluminum alloy section for cylinder | |
| CN115109974A (en) | Al-Cu-Li-Zr-Ce-Sc alloy plate with ultrahigh strength and good plasticity and preparation method thereof | |
| CN113881877A (en) | Aluminum alloy strip and preparation method and application thereof | |
| RU2287600C1 (en) | Aluminum-base material | |
| CN113528903A (en) | 5052 aluminum alloy with high bending performance and preparation method thereof | |
| CN113106365B (en) | Annealing method of 2219 aluminum alloy ingot and 2219 aluminum alloy deformation piece | |
| JP3516566B2 (en) | Aluminum alloy for cold forging and its manufacturing method | |
| CN111378869A (en) | Fine-grain reinforced brass strip for connector and processing method thereof | |
| JP3840400B2 (en) | Method for producing semi-melt molded billet of aluminum alloy for transportation equipment | |
| CN114525421A (en) | Magnesium alloy and preparation method and application thereof | |
| JPH02247348A (en) | Heat-resistant aluminum alloy having excellent tensile strength, ductility and fatigue resistance | |
| CN113278827A (en) | Medium-strength easily-extruded 5-series aluminum alloy ingot | |
| JPH11350058A (en) | Aluminum alloy sheet excellent in formability and baking hardenability and its production | |
| JP3798676B2 (en) | Method for producing semi-melt molded billet of aluminum alloy for transportation equipment | |
| CN110983101A (en) | High-yield high-ductility medium-high-entropy alloy and preparation method thereof | |
| CN115896537B (en) | High-strength corrosion-resistant Cu-Ni-Sn alloy and preparation method thereof | |
| JP4152095B2 (en) | Method for producing semi-molten billet of aluminum alloy for transportation equipment | |
| CN114672674B (en) | Casting-rolling high-strength high-toughness aluminum-silicon alloy and preparation method thereof | |
| CN115418540B (en) | Large-specification high-strength high-toughness board and preparation method thereof | |
| JPH09176805A (en) | Production of aluminum fin material |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant | ||
| TR01 | Transfer of patent right | ||
| TR01 | Transfer of patent right |
Effective date of registration: 20221114 Address after: 363 Changxing Road, Tianhe District, Guangzhou, Guangdong 510000 Patentee after: Institute of new materials, Guangdong Academy of Sciences Address before: 510000 363 Changxin Road, Tianhe District, Guangzhou, Guangdong. Patentee before: Institute of materials and processing, Guangdong Academy of Sciences |