CN114107848A - Method for reducing residual stress of aluminum alloy thin-wall component - Google Patents
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- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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Abstract
The invention discloses a method for reducing residual stress of an aluminum alloy thin-wall component, which is characterized by comprising the following steps of: the aluminum alloy comprises, by mass, 5.0-7.0% of Zn, 1.0-5% of Mg, 1.0-5.0% of Cu, and the balance of Al and inevitable impurities; the preparation process flow of the aluminum alloy comprises the following steps: solid solution → extrusion → aging → stress relief annealing, the final temperature of the stress relief annealing is TFinal (a Chinese character of 'gan')The initial temperature of the stress relief annealing is TStarting pointThe time required for the temperature rise from the initial temperature to the final temperature is tLifting of wineThe required temperature rise rate is VLifting of wine，TStarting point＝TFinal (a Chinese character of 'gan')‑VLifting of wine×tLifting of wineWherein V isLifting of wineIn units of ℃/h, tLifting of wineThe unit of (d) is h. The non-isothermal heat treatment method of the aluminum alloy thin-wall component with the temperature rise speed and the temperature drop speed has the advantages of good stress removal effect, small influence on the mechanical property of the aluminum alloy component and extremely low deformation degree of the component.
Description
Technical Field
The invention relates to the technical field of aluminum alloy materials, in particular to a method for reducing residual stress of an aluminum alloy thin-wall component.
Background
The Al-Zn-Mg-Cu aluminum alloy has the characteristics of small density, high strength, good toughness and corrosion resistance, excellent processability and welding performance and the like, is an important structural material for lightweight design and comprehensive performance improvement of aircrafts, vehicles, tools and the like, is widely applied to the industries of transportation, electronics, bridges, decoration and the like, and is the first use amount of non-ferrous metal materials. In addition, the aluminum alloy has wide application prospect and irreplaceable status in aerospace, ship, nuclear industry and weapon industry, so the high-strength aluminum alloy technology is listed as a key technology of national defense science and technology and a basic technology of key development. The tensile strength of the Al-Zn-Mg-Cu aluminum alloy is generally higher than 500MPa, wherein the 7A04 aluminum alloy is a well-developed, long-term and wide alloy in the Al-Zn-Mg-Cu aluminum alloy, and has the advantages of high strength, good heat treatment strengthening effect, moderate plasticity in annealing and new quenching states and the like.
With the development of damage tolerance design technologies for structural members in industries such as aviation, transportation, instruments and meters, the requirements for high-strength aluminum alloy structural members are higher and higher, the strength of materials is required to be high, and the quality of the structural members is required to be smaller and better in many occasions, so that the high-strength aluminum alloy thin-wall structural members are applied more and more. As the wall thickness of the high-strength aluminum alloy member is reduced, the structural rigidity of the high-strength aluminum alloy member is weakened, and the influence of the residual machining stress formed in the manufacturing process of the member on the characteristics of the member, such as shape, size and the like, is more and more serious, so that the technical demand for controlling the residual stress of the high-strength aluminum alloy member is urgent.
High strength aluminum alloys such as Al-Zn-Mg-Cu series and the like usually require solution treatment and aging treatment to obtain high strength and toughness. When a material is rapidly cooled from a high temperature of about 500 ℃ to a lower temperature, a large thermal stress gradient is introduced during cooling, and generally the surface of the component exhibits compressive stress and the interior exhibits tensile stress. The research results show that the residual stress generated by quenching in the solution treatment of the aluminum alloy is even close to the yield limit of the material. The stress distribution is related to the size and geometry of the component, and when the shape is complex and the thickness is not uniform, a complex stress distribution state is caused. In some high-strength aluminum alloy components, in order to further improve the strength of the components, cold drawing or other cold working deformation is carried out after solution treatment, and then, dislocations are further introduced into the components, which causes microstructure lattice distortion, and the tendency is gradually strengthened along with the increase of the cold working deformation amount, namely the increase of dislocation density, so that the residual stress in the components is greatly improved.
At present, the approaches for reducing the residual stress of the high-strength aluminum alloy component mainly comprise two main types of heat treatment methods and mechanical treatment methods, specifically: aging treatment, mechanical stretching, cryogenic treatment, vibration elimination, and molding. The heat treatment method is a traditional method for reducing quenching residual stress, but the effect of eliminating the residual stress is not ideal. Because the aluminum alloy material is very sensitive to temperature, the strength index is inevitably obviously reduced by increasing the heat treatment temperature, and MgZn is changed2Precipitation of equi-strengthening phases, which can have adverse effects. For example, the aging treatment after quenching is carried out at a relatively low temperature (less than 200 to 250 ℃), so that the residual stress eliminating effect is only 10 to 35%, which is very limited.
Disclosure of Invention
The invention aims to provide a method for reducing residual stress of an aluminum alloy thin-wall component.
The present invention solves the above technical problemsThe technical scheme is as follows: a method for reducing residual stress of an aluminum alloy thin-wall component is characterized by comprising the following steps: the aluminum alloy comprises, by mass, 5.0-7.0% of Zn, 1.0-5% of Mg, 1.0-5.0% of Cu, and the balance of Al and inevitable impurities; the preparation process flow of the aluminum alloy comprises the following steps: solid solution → extrusion → aging → stress relief annealing, the final temperature of the stress relief annealing is TFinal (a Chinese character of 'gan')The initial temperature of the stress relief annealing is TStarting pointThe time required for the temperature rise from the initial temperature to the final temperature is tLifting of wineThe required temperature rise rate is VLifting of wine，TStarting point＝TFinal (a Chinese character of 'gan')-VLifting of wine×tLifting of wineWherein V isLifting of wineIn units of ℃/h, tLifting of wineHas the unit of h, TFinal (a Chinese character of 'gan')At 150-200 ℃ and VLifting of wineIs 20 ℃/h-50 ℃/h, tLifting of wine1 to 3 hours from TStarting pointTo TFinal (a Chinese character of 'gan')Then the heat preservation is carried out for a heat preservation time THealth-care product1-10 min, after the heat preservation is finished, according to VDescend＝VLifting of wineCooling rate to TStarting pointFrom TStarting point→TFinal (a Chinese character of 'gan')→TStarting pointThe period can be carried out once or can be circulated twice or more for one period of stress relief annealing, and finally the component is cooled in the furnace.
The heating rate and the cooling rate of the heat treatment of the aluminum alloy member have important influence on the residual stress of the member, and the heating rate and the cooling rate are controlled to be 20-50 ℃/h. The temperature rise speed/temperature drop speed is too low, which is beneficial to the slow release of residual stress and the reduction of the deformation degree of the component, but can cause too long heat treatment time and influence the treatment efficiency; the temperature rise speed/cooling speed is too high, the precipitated phase of the aluminum alloy grows up and is accelerated, the mechanical property of the component is not influenced, the residual stress of the aluminum alloy component is released too fast, the deformation degree of the component is aggravated, the temperature rise speed/cooling speed is increased, the heat treatment time is shortened, the residual stress is difficult to fully release, and the treatment effect is influenced.
Preferably, the thickness of the aluminum alloy thin-walled member is 0.01mm to 10 mm.
Preferably, the cycle period of the stress relief annealing is 2-10 times. Since the residual stress eliminating effect of the aluminum alloy thin-walled member hardly satisfies the design requirement in one heat treatment cycle, a plurality of heat treatment cycles can be performed so that the residual stress eliminating effect satisfies the design requirement.
Preferably, the microstructure of the aluminum alloy thin-walled member contains precipitated phases of eta' phase and eta phase, and the precipitated phase area ratio of 0.1 μm or less in size is 30 to 40%, the precipitated phase area ratio of more than 0.1 μm and 1 μm or less is 50 to 60%, and the precipitated phase area ratio of 5 μm or more is less than 1%.
Preferably, the residual stress of the aluminum alloy thin-walled member is tensile stress, the axial residual stress is 70MPa or less, the radial residual stress is 50MPa or less, and the Vickers hardness is 120HV or more.
Compared with the prior art, the invention has the advantages that: according to the non-isothermal heat treatment method for the aluminum alloy thin-wall member, disclosed by the invention, the aluminum alloy has a precipitation behavior in the process, due to the controlled increase or decrease of the temperature, thermodynamic parameters of an aluminum alloy precipitation phase, such as a diffusion coefficient, a critical nucleation size and the like, are a dynamic change process, the competition relationship of the aluminum alloy precipitation phase is very obvious, and strain energy in the aluminum alloy can be consumed through the precipitation of the aluminum alloy phase, so that the residual stress in the aluminum alloy is orderly relaxed, the residual stress of the aluminum alloy thin-wall member is greatly reduced, the stress removal effect is good, the influence on the mechanical property of the aluminum alloy member is small, and the deformation degree of the member is extremely low.
Detailed Description
The present invention will be described in further detail with reference to examples.
The invention provides 4 examples and 1 comparative example, and the specific components are shown in Table 1.
The first embodiment is as follows:
the aluminum alloy thin-walled member of the present embodiment is cylindrical and has a length of
An outer diameter of
An inner diameter of
With a variable cross-section, a cylinder bottom thickness of
The component blank is a cup-shaped part with the inner diameter of 29.2mm, the wall thickness of 4.0mm and the height of 40.0 mm; the preparation process comprises the following steps: after the blank is subjected to solution treatment, hot spinning forming is carried out at 380 ℃, artificial aging is carried out at 120 ℃, and then stress relief annealing is carried out.
The method for eliminating the residual stress of the aluminum alloy component comprises the following steps:
(1) final temperature T of aluminum alloyFinal (a Chinese character of 'gan')Determination of (A), TFinal (a Chinese character of 'gan')At 180 ℃ tLifting of wineWhich is 7000 s.
(2) Heat treatment time T for aluminium alloyHealth-care productIs determined
The wall thickness of the aluminum alloy component is 0.9 mm-2.3 mm, and the heat preservation time is determined to be 5 min.
(3) Temperature rise speed V of aluminum alloy heat treatmentLifting of wineAnd the cooling rate VDescendIs determined
The rate of temperature rise and the rate of temperature fall of the aluminum alloy member heat treatment were determined to be 50 ℃/h.
(4) Heat treatment starting temperature T of aluminum alloyStarting pointIs determined
According to the formula TStarting point＝TFinal (a Chinese character of 'gan')-VLifting of wine×tLifting of wineT can be obtained by calculationStarting point：
TStarting point＝180-(7000/3600)×50＝82.8℃≈83℃
(5) Stress relief annealing of aluminum alloy thin-walled components
According to the heat treatment process parameters, the heat treatment furnace is firstly heated to the initial temperature of 83 ℃, the aluminum alloy member is put into the furnace, and the heating is started according to the specified heating speed until the final temperature is 180 ℃. After the heat preservation is carried out for 5min, the temperature is reduced according to the specified cooling speed until the initial temperature is 83 ℃. At this point, a heat treatment cycle is completed.
This example measured the residual stress of the thin-walled aluminum alloy member before and after the heat treatment after five heat treatment cycles
(the measurement point is on the circumferential outer surface at a height of 70mm from the bottom), and the results are shown in Table 2, and the dimensions of the heat-treated aluminum alloy structural member were measured and all met the dimensional requirements.
Example two:
the aluminum alloy thin-walled member of the present embodiment is cylindrical and has a length of
An outer diameter of
An inner diameter of
With a variable cross-section, a cylinder bottom thickness of
The component blank is a cup-shaped part with the inner diameter of 29.2mm, the wall thickness of 4.0mm and the height of 40.0 mm; the preparation process comprises the following steps: after the blank is subjected to solution treatment, hot spinning forming is carried out at 380 ℃, artificial aging is carried out at 120 ℃, and then stress relief annealing is carried out.
The step of eliminating residual stress of the aluminum alloy member is described in example 1, and is not described herein.
TFinal (a Chinese character of 'gan')At 180 ℃ tLifting of wine7000s, holding time THealth-care productDetermined as 5min, temperature rising speed VLifting of wineAnd the cooling rate VDescendDetermined as 20 ℃/h according to the formula TStarting point＝TFinal (a Chinese character of 'gan')-VLifting of wine×tLifting of wineT can be obtained by calculationStarting point＝180-(7000/3600)×20＝141.1℃≈141℃
And (3) stress relief annealing according to the heat treatment process parameters, firstly heating the heat treatment furnace to the initial temperature of 141 ℃, putting the aluminum alloy member into the furnace, and heating at a specified heating rate until the final temperature is 180 ℃. After the heat preservation is carried out for 5min, the temperature is reduced according to the specified cooling speed until the initial temperature is 141 ℃. At this point, a heat treatment cycle is completed.
In the present example, two heat treatment cycles were designed, and the residual stress (measured at the circumferential outer surface at a height of 70mm from the bottom) of the aluminum alloy thin-walled member before and after the heat treatment was as shown in table 2, and the dimension of the aluminum alloy member after the heat treatment was measured and was in accordance with the dimensional requirement.
Example three:
the aluminum alloy thin-walled member of the present embodiment is cylindrical and has a length of
An outer diameter of
An inner diameter of
With a variable cross-section, a cylinder bottom thickness of
The component blank is a cup-shaped part with the inner diameter of 29.2mm, the wall thickness of 4.0mm and the height of 40.0 mm; the preparation process comprises the following steps: after the blank is subjected to solution treatment, hot spinning forming is carried out at 380 ℃, artificial aging is carried out at 125 ℃, and then stress relief annealing is carried out.
The step of eliminating residual stress of the aluminum alloy member is described in example 1, and is not described herein.
TFinal (a Chinese character of 'gan')At 180 ℃ tLifting of wine7200s, heat preservation time THealth-care productDetermined as 5min, temperature rising speed VLifting of wineAnd the cooling rate VDescendIs determined to be 40 ℃/h according to the formula TStarting point＝TFinal (a Chinese character of 'gan')-VLifting of wine×tLifting of wineT can be obtained by calculationStarting point＝180-(7200/3600)×40＝100℃
And (3) stress relief annealing according to the heat treatment process parameters, firstly heating the heat treatment furnace to the initial temperature of 100 ℃, putting the aluminum alloy member into the furnace, and starting heating at a specified heating rate until the final temperature is 180 ℃. After preserving the heat for 5min, cooling at a specified cooling speed until the initial temperature is 100 ℃. At this point, a heat treatment cycle is completed.
In the embodiment, three heat treatment cycles are designed, the residual stress (measured point is on the circumferential outer surface at the position 70mm away from the bottom) of the aluminum alloy thin-wall member before and after heat treatment is shown in table 2, and the dimension of the aluminum alloy member after heat treatment is measured and meets the dimension requirement.
Example four:
the aluminum alloy thin-walled member of the present embodiment is cylindrical and has a length of
An outer diameter of
An inner diameter of
With a variable cross-section, a cylinder bottom thickness of
The component blank is a cup-shaped piece with the inner diameter of 29.2mm, the wall thickness of 4mm and the height of 40 mm; the preparation process comprises the following steps: after the blank is subjected to solution treatment, hot spinning forming is carried out at 380 ℃, artificial aging is carried out at 125 ℃, and then stress relief annealing is carried out.
The step of eliminating residual stress of the aluminum alloy member is described in example 1, and is not described herein.
TFinal (a Chinese character of 'gan')At 182 ℃ tLifting of wine7500s, heat preservation time THealth-care productDetermined as 5min, temperature rising speed VLifting of wineAnd the cooling rate VDescendIs determined to be 30 ℃/h according to the formula TStarting point＝TFinal (a Chinese character of 'gan')-VLifting of wine×tLifting of wineT can be obtained by calculationStarting point＝182-(7500/3600)×30＝119.5℃≈120℃。
And (3) stress relief annealing according to the heat treatment process parameters, firstly heating the heat treatment furnace to the initial temperature of 120 ℃, putting the aluminum alloy member into the furnace, and starting heating at the specified heating rate until the final temperature is 182 ℃. After preserving the heat for 5min, cooling at a specified cooling speed until the initial temperature is 120 ℃. At this point, a heat treatment cycle is completed.
In the embodiment, three heat treatment cycles are designed, the residual stress (measured point is on the circumferential outer surface at the position 70mm away from the bottom) of the aluminum alloy thin-wall member before and after heat treatment is shown in table 2, and the dimension of the aluminum alloy member after heat treatment is measured and meets the dimension requirement.
Comparative example 1: unlike the process of example 1 without subsequent artificial aging and stress relief annealing.
Comparative example 2: unlike the process of example 1, there is no subsequent stress relief anneal.
The values of the compressive residual stress of the aluminum alloy members obtained in the first to fourth examples and the comparative example are shown in Table 2, wherein positive values represent the tensile residual stress and negative values represent the compressive residual stress.
TABLE 1 chemical compositions and microstructures of inventive and comparative examples
TABLE 2 mechanical Properties of inventive and comparative examples
Claims (5)
1. A method for reducing residual stress of an aluminum alloy thin-wall component is characterized by comprising the following steps: the aluminum alloy comprises, by mass, 5.0-7.0% of Zn, 1.0-5% of Mg, 1.0-5.0% of Cu, and the balance of Al and inevitable impurities; the preparation process flow of the aluminum alloy comprises the following steps: solid solution → extrusion → aging → stress relief annealing, the final temperature of the stress relief annealing is TFinal (a Chinese character of 'gan')The initial temperature of the stress relief annealing is TStarting pointThe time required for the temperature rise from the initial temperature to the final temperature is tLifting of wineThe required temperature rise rate is VLifting of wine，TStarting point＝TFinal (a Chinese character of 'gan')-VLifting of wine×tLifting of wineWherein V isLifting of wineIn units of ℃/h, tLifting of wineHas the unit of h, thenT isFinal (a Chinese character of 'gan')At 150-200 ℃ and VLifting of wineIs 20 ℃/h-50 ℃/h, tLifting of wine1 to 3 hours from TStarting pointTo TFinal (a Chinese character of 'gan')Then the heat preservation is carried out for a heat preservation time THealth-care product1-10 min, after the heat preservation is finished, according to VDescend＝VLifting of wineCooling rate to TStarting pointFrom TStarting point→TFinal (a Chinese character of 'gan')→TStarting pointThe period can be carried out once or can be circulated twice or more for one period of stress relief annealing, and finally the component is cooled in the furnace.
2. The method of reducing residual stress in an aluminum alloy thin walled component of claim 1, wherein: the wall thickness of the aluminum alloy thin-wall component is 0.01 mm-10 mm.
3. The method of reducing residual stress in an aluminum alloy thin walled component of claim 1, wherein: the cycle period of the stress relief annealing is 2-10 times.
4. The method of reducing residual stress in an aluminum alloy thin walled component of claim 1, wherein: the microstructure of the aluminum alloy thin-walled member contains eta' phase and eta phase precipitated phase, the precipitated phase area ratio of the size below 0.1 mu m is 30-40%, the precipitated phase area ratio of more than 0.1 mu m and less than or equal to 1 mu m is 50-60%, and the precipitated phase area ratio of more than 5 mu m is less than 1%.
5. The method of reducing residual stress of an aluminum alloy thin walled component according to any of claims 1 to 4, wherein: the residual stress of the aluminum alloy thin-wall component is tensile stress, the axial residual stress is below 70MPa, the radial residual stress is below 50MPa, and the Vickers hardness is above 120 HV.
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Cited By (1)
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| CN115125384A (en) * | 2022-05-31 | 2022-09-30 | 山西北方机械制造有限责任公司 | High-precision variable-cross-section pipe part heat treatment self-correcting method |
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| CN115125384A (en) * | 2022-05-31 | 2022-09-30 | 山西北方机械制造有限责任公司 | High-precision variable-cross-section pipe part heat treatment self-correcting method |
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