CN115433889A - Intermittent non-isothermal aging treatment process for aluminum alloy - Google Patents
Intermittent non-isothermal aging treatment process for aluminum alloy Download PDFInfo
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Abstract
The invention relates to an aluminum alloy intermittent non-isothermal aging treatment process, belonging to the field of aluminum alloy heat treatment. The method is characterized in that: the process method comprises solution quenching, primary non-isothermal aging, quenching, secondary non-isothermal aging and quenching treatment. The secondary non-isothermal aging treatment at a lower temperature enables the aluminum alloy to generate a secondary precipitation phenomenon in a shorter time, and the secondary precipitation phase is large in quantity and small in size. After the aluminum alloy adopts the process method, the intragranular precipitated phase of the alloy is fine and dispersed, and the grain boundary precipitated phase is discontinuously distributed. The invention ensures that the aluminum alloy obtains good mechanical property and corrosion resistance in a short time, improves the production efficiency and is worth popularizing and using later.
Description
Technical Field
The invention belongs to the field of heat treatment of aluminum alloy, and particularly relates to an intermittent non-isothermal aging treatment process for aluminum alloy.
Background
Aluminum alloys are often used in the industrial fields of automobiles, aviation, and the like because of their low density and high strength. However, aluminum alloys are prone to local corrosion phenomena such as pitting corrosion and intergranular corrosion in a wet environment, which limits their industrial application. In recent years, in order to provide an aluminum alloy with both good mechanical properties and corrosion resistance, researchers have developed heat treatment processes such as retrogradation. However, the treatment time of the regression and reaging treatment process is longer, so that the production efficiency of the high-performance aluminum alloy is greatly reduced. Therefore, it is very important to develop a heat treatment process which can simultaneously improve the mechanical properties and corrosion resistance of the aluminum alloy and shorten the treatment time.
Disclosure of Invention
The purpose of the invention is as follows: the invention provides an aluminum alloy intermittent non-isothermal aging treatment process, and aims to ensure that an aluminum alloy obtains high mechanical property and good corrosion resistance simultaneously under the condition of shortening the aging treatment time, and improve the production efficiency of the high-performance aluminum alloy in the actual industrial production process.
The technical scheme is as follows:
an intermittent non-isothermal aging treatment process for aluminum alloy, which is applicable to aging-strengthened aluminum alloy, and is characterized in that: the process comprises the following steps:
firstly, solution treatment; placing the aluminum alloy at the temperature of 450-560 ℃ for a period of time until most of the components of the aluminum alloy are dissolved in the matrix, thereby forming a supersaturated solid solution;
secondly, quenching treatment; transferring the aluminum alloy into a proper fluid to rapidly cool the aluminum alloy to room temperature and inhibit the precipitation of components in a supersaturated solid solution;
thirdly, carrying out primary non-isothermal aging treatment; placing the aluminum alloy at the Ta temperature of the traditional artificial aging treatment, and increasing the temperature from the Ta temperature to the Tb temperature at the va rate;
step four, quenching treatment; transferring the aluminum alloy into a suitable fluid to rapidly cool the aluminum alloy to room temperature;
fifthly, secondary non-isothermal aging treatment; placing the aluminum alloy at the Tc temperature, and increasing the temperature from the Tc temperature to the Td temperature at the vb rate;
sixthly, quenching treatment; transferring the aluminum alloy into a proper fluid to rapidly cool the aluminum alloy to room temperature to obtain a heat-treated aluminum alloy;
the Ta temperature of the traditional artificial aging treatment is within the range of 100-190 ℃, the Tb temperature is within the range of 200-380 ℃, the Tc temperature is less than 190 ℃, the Td temperature is less than 380 ℃, and the temperature rise rates of va and vb are within the range of 3-30 ℃/h.
Preferably, the transfer time of the quenching treatment of the second, fourth and sixth steps of the step should not exceed 15 s.
Preferably, the fluid for quenching treatment in the second step, the fourth step and the sixth step is water or polymer organic quenching liquid.
Preferably, the first non-isothermal ageing treatment of the third step is an incomplete ageing treatment.
Preferably, in the third step of the first-stage non-isothermal aging treatment, the Tb temperature should be less than 2 × Ta temperature.
Preferably, in the fifth step of the second-stage non-isothermal aging treatment, the Tc temperature should be lower than the Ta temperature of the conventional artificial aging treatment.
Preferably, in the fifth step of the second non-isothermal aging treatment, the Td temperature should be <2 × Tc temperature.
Preferably, if the heat-treated aluminum alloy obtained in the sixth step is not fully aged, the fifth step and the sixth step may be repeated after the sixth step for a plurality of times until the heat-treated aluminum alloy reaches a fully aged condition.
The invention has the following advantages and positive effects:
1. the invention can increase the amount of the precipitation phase in the aluminum alloy, and the precipitation phase is fine and dispersed, good in roundness of the crystal boundary precipitation phase and discontinuously distributed. Thereby leading the aluminum alloy to obtain high mechanical property and high corrosion resistance simultaneously.
2. The invention can reduce the time of aging treatment, save the cost and improve the production efficiency.
Drawings
FIG. 1 is an intergranular corrosion morphology of a 2 xxx-series aluminum alloy obtained in example 1;
FIG. 2 is an intergranular corrosion morphology of the 2 xxx-series aluminum alloy obtained in example 2;
FIG. 3 is an intergranular corrosion morphology of the 2 xxx-series aluminum alloy obtained in example 3;
FIG. 4 is an intergranular corrosion morphology of the 7 xxx-series aluminum alloy obtained in example 4;
FIG. 5 is an intergranular corrosion morphology of the 7 xxx-series aluminum alloy obtained in example 5;
FIG. 6 is an intergranular corrosion morphology of the 7 xxx-series aluminum alloy obtained in example 6;
FIG. 7 is an intergranular corrosion morphology of the 7xxx aluminum alloy obtained in example 7;
FIG. 8 is a bright field transmission electron microscope image of a 7 xxx-series aluminum alloy obtained in example 7.
Detailed Description
The principle of the intermittent non-isothermal aging technology is that secondary temperature rise is utilized, so that secondary precipitation occurs to the aluminum alloy under the condition of saving aging time, and the mechanical property and the corrosion resistance of the alloy are further improved. After the aluminum alloy is subjected to solution quenching, primary non-isothermal aging treatment is carried out, GP zones and metastable phases are rapidly formed in the early stage of aging, the solid solubility of the alloy is increased along with the gradual increase of the aging temperature, and the precipitated phases of nucleation are less and less. The alloy is quenched and then subjected to secondary non-isothermal aging treatment, the temperature of the alloy is lower than that of the primary non-isothermal aging treatment, secondary precipitation can occur to the aluminum alloy, and new GP zones and metastable phase nuclei grow. The aluminum alloy subjected to the intermittent non-isothermal aging treatment has fine and dispersed intragranular precipitated phases, and the grain boundary precipitated phases are in a chain shape.
The specific technical scheme is as follows:
firstly, solution treatment; placing the aluminum alloy at the temperature of 450-560 ℃ for a period of time until most of the components of the aluminum alloy are dissolved in the matrix, thereby forming a supersaturated solid solution;
step two, quenching treatment; transferring the aluminum alloy into a proper fluid to quickly cool the aluminum alloy to room temperature and inhibit the precipitation of components in a supersaturated solid solution;
thirdly, carrying out primary non-isothermal aging treatment; placing the aluminum alloy at the Ta temperature of the traditional artificial aging treatment, and increasing the temperature from the Tc temperature to the Tb temperature at the va rate;
step four, quenching treatment; transferring the aluminum alloy into a suitable fluid to rapidly cool the aluminum alloy to room temperature;
fifthly, secondary non-isothermal aging treatment; placing the aluminum alloy at the Tc temperature, and increasing the temperature from the Tc temperature to the Td temperature at the vb rate;
sixthly, quenching treatment; transferring the aluminum alloy into a proper fluid to rapidly cool the aluminum alloy to room temperature to obtain a heat-treated aluminum alloy;
the Ta temperature of the traditional artificial aging treatment is within the range of 100-190 ℃, the Tb temperature is within the range of 200-380 ℃, the Tc temperature is less than 190 ℃, the Td temperature is less than 380 ℃, and the temperature rise rates of va and vb are within the range of 3-30 ℃/h.
In the above technical scheme:
preferably, the transfer time of the quenching treatment of the second, fourth and sixth steps of the step should not exceed 15 s.
Preferably, the fluid for quenching treatment in the second step, the fourth step and the sixth step is water or polymer organic quenching liquid.
Preferably, the first-stage non-isothermal aging treatment in the third step is incomplete aging treatment.
Preferably, in the third step of the first-stage non-isothermal aging treatment, the Tb temperature should be less than 2 × Ta temperature.
Preferably, in the fifth step of the second-stage non-isothermal aging treatment, the Tc temperature should be lower than the Ta temperature of the conventional artificial aging treatment.
Preferably, in the fifth step of the second non-isothermal aging treatment, the Td temperature should be less than 2 × Tc temperature.
Preferably, if the heat-treated aluminum alloy obtained in the sixth step is not fully aged, the fifth step and the sixth step may be repeated after the sixth step until the heat-treated aluminum alloy reaches the fully aged condition.
The invention is illustrated by specific examples:
the mass components of the 2 xxx-series aluminum alloys in examples 1, 2 and 3 were: 4.78% of copper, 1.52% of magnesium, 0.48% of manganese, 0.28% of iron, 0.13% of silicon and the balance of aluminum.
Example 1:
firstly, putting 2xxx series aluminum alloy into a box type resistance furnace at 500 ℃ and preserving heat for 40 min;
secondly, transferring the alloy into deionized water at 0 to 5 ℃ within 5 seconds, and cooling the alloy;
thirdly, putting the powder into a digital constant-temperature air-blast drying oven at 190 ℃ and raising the temperature to 250 ℃ at the rate of 18 ℃/h;
fourthly, transferring the alloy into deionized water at 0 to 5 ℃ within 5 seconds, and cooling the alloy;
fifthly, putting the materials into a digital constant-temperature air-blowing drying box at 80 ℃, and raising the temperature to 140 ℃ at the speed of 15 ℃/h;
and sixthly, transferring the alloy to deionized water at 0-5 ℃ within 5 seconds, and cooling the alloy to obtain the heat-treated aluminum alloy.
The surface hardness of the aluminum alloy was 156.4 HV, the tensile strength was 452 MPa, and the elongation was 10.8%. As shown in FIG. 1, the depth of intergranular corrosion of the aluminum alloy was 72 μm.
Example 2:
firstly, putting 2xxx series aluminum alloy into a box type resistance furnace at 500 ℃ and preserving heat for 40 min;
secondly, transferring the alloy into normal-temperature polymer organic quenching liquid within 5 s, and cooling the alloy;
thirdly, putting the powder into a digital constant-temperature air-blast drying oven at 190 ℃ and raising the temperature to 250 ℃ at a rate of 24 ℃/h;
fourthly, transferring the alloy into normal-temperature polymer organic quenching liquid within 5 seconds, and cooling the alloy;
fifthly, putting the mixture into a digital constant-temperature air-blast drying oven at 80 ℃, and raising the temperature to 140 ℃ at the rate of 18 ℃/h;
and sixthly, transferring the alloy to normal-temperature polymer organic quenching liquid within 5 s, and cooling the alloy to obtain the heat-treated aluminum alloy.
The polymer organic quenching liquid is a conventional quenching liquid, such as: oil organic quenching liquid, PAG organic quenching liquid and the like.
The surface hardness of the aluminum alloy is 152.0 HV, the tensile strength is 442 MPa, and the elongation is 9.6%. As shown in FIG. 2, the depth of intergranular corrosion of the aluminum alloy was 67 μm.
As can be seen from the comparison between the example 1 and the example 2, the higher temperature rise rates va and vb can make the roundness of the grain boundary precipitated phase better, the chain distribution is obvious, the corrosion resistance of the alloy is further improved, and the mechanical property of the alloy is not changed greatly.
Example 3:
firstly, putting 2xxx series aluminum alloy into a box type resistance furnace at 500 ℃ and preserving heat for 40 min;
secondly, transferring the alloy into deionized water at 0 to 5 ℃ within 5 seconds, and cooling the alloy;
thirdly, putting the powder into a digital constant-temperature air-blast drying oven at 190 ℃ and raising the temperature to 250 ℃ at a rate of 15 ℃/h;
fourthly, transferring the alloy into deionized water at 0 to 5 ℃ within 5 seconds, and cooling the alloy;
fifthly, putting the materials into a digital constant-temperature air-blowing drying box at 80 ℃, and raising the temperature to 140 ℃ at the speed of 12 ℃/h;
and sixthly, transferring the alloy to deionized water at 0-5 ℃ within 5 seconds, and cooling the alloy to obtain the heat-treated aluminum alloy.
The surface hardness of the aluminum alloy was 148.6 HV, the tensile strength was 426 MPa, and the elongation was 9.2%. As shown in FIG. 3, the depth of intergranular corrosion of the aluminum alloy was 35 μm.
As can be seen from the comparison between the example 1 and the example 3, the decrease of the temperature rise rates va and vb may cause coarsening of the intergranular precipitated phase, the intergranular precipitated phase is distributed intermittently, the mechanical properties of the alloy are slightly decreased, and the corrosion resistance is further improved.
The 7xxx aluminum alloys of examples 4, 5, 6, and 7 have the following composition by mass: 5.91% of zinc, 2.4% of magnesium, 1.5% of copper, 0.18% of chromium, 0.17% of iron, 0.09% of silicon, 0.03% of manganese and the balance of aluminum.
Example 4:
firstly, placing 7xxx series aluminum alloy into a box type resistance furnace at 470 ℃ for heat preservation for 1 h, and then placing the box type resistance furnace at 450 ℃ for heat preservation for 2 h;
secondly, transferring the alloy into deionized water at 0 to 5 ℃ within 3 seconds, and cooling the alloy;
thirdly, putting the mixture into a digital constant-temperature air-blast drying oven at 100 ℃, and raising the temperature to 180 ℃ at the speed of 12 ℃/h;
fourthly, transferring the alloy into deionized water at 0 to 5 ℃ within 3 seconds, and cooling the alloy;
fifthly, putting the materials into a 60 ℃ digital constant temperature air blast drying box, and raising the temperature to 100 ℃ at the speed of 12 ℃/h;
and sixthly, transferring the alloy to deionized water at 0-5 ℃ within 3 seconds, and cooling the alloy to obtain the heat-treated aluminum alloy.
The surface hardness of the aluminum alloy was 202.8 HV, the tensile strength was 484 MPa, and the elongation was 10.4%. As shown in FIG. 4, the depth of intergranular corrosion of the aluminum alloy was 84 μm.
Example 5:
firstly, placing 7xxx series aluminum alloy into a box type resistance furnace at 470 ℃ for heat preservation for 1 h, and then placing the box type resistance furnace at 450 ℃ for heat preservation for 2 h;
secondly, transferring the alloy into deionized water at 0 to 5 ℃ within 8 seconds, and cooling the alloy;
thirdly, putting the mixture into a 120 ℃ digital constant-temperature air-blast drying box, and raising the temperature to 200 ℃ at the speed of 12 ℃/h;
fourthly, transferring the alloy into deionized water at 0 to 5 ℃ within 8 s, and cooling the alloy;
fifthly, putting the mixture into a 60 ℃ digital constant-temperature air-blast drying oven, and raising the temperature to 100 ℃ at the speed of 12 ℃/h;
and sixthly, transferring the alloy to deionized water at 0-5 ℃ within 8 seconds, and cooling the alloy to obtain the heat-treated aluminum alloy.
The surface hardness of the aluminum alloy is 194.6 HV, the tensile strength is 468 MPa, and the elongation is 10.7%. As shown in FIG. 5, the depth of intergranular corrosion of the aluminum alloy was 43 μm.
As can be seen from the comparison between the example 4 and the example 5, the increase of the initial temperature Ta and the final temperature Tb of the primary non-isothermal aging treatment may cause coarsening of the intergranular precipitated phase, and the discontinuity of the intergranular precipitated phase is obvious, so that the hardness and the strength of the aluminum alloy are slightly reduced, the corrosion depth is reduced, and the corrosion resistance is improved.
Example 6:
firstly, placing 7xxx series aluminum alloy into a box type resistance furnace at 470 ℃ for heat preservation for 1 h, and then placing the box type resistance furnace at 450 ℃ for heat preservation for 2 h;
secondly, transferring the alloy into normal-temperature polymer organic quenching liquid within 12 seconds, and cooling the alloy;
thirdly, putting the mixture into a 120 ℃ digital constant-temperature air-blast drying box, and raising the temperature to 200 ℃ at the speed of 12 ℃/h;
fourthly, transferring the alloy into normal-temperature polymer organic quenching liquid within 12 seconds, and cooling the alloy;
fifthly, putting the mixture into a digital constant-temperature air-blast drying oven at 80 ℃, and raising the temperature to 120 ℃ at the speed of 12 ℃/h;
and sixthly, transferring the alloy to normal-temperature polymer organic quenching liquid within 12 seconds, and cooling the alloy to obtain the heat-treated aluminum alloy.
The surface hardness of the aluminum alloy is 190.8 HV, the tensile strength is 442 MPa, and the elongation is 9.8%. As shown in FIG. 6, the depth of intergranular corrosion of the aluminum alloy was 41 μm.
It is known from comparison between example 5 and example 6 that the higher temperature of the secondary non-isothermal aging treatment of the aluminum alloy may cause too fast nucleation of GP zones and metastable phases, the less secondary precipitated phases and the possibility of coarsening, and the mechanical properties of the aluminum alloy are further reduced, but the intergranular corrosion depth is slightly reduced and the corrosion resistance is enhanced.
Example 7:
firstly, placing 7xxx series aluminum alloy into a box type resistance furnace at 470 ℃ for heat preservation for 1 h, and then placing the box type resistance furnace at 450 ℃ for heat preservation for 2 h;
secondly, transferring the alloy into deionized water at 0 to 5 ℃ within 3 seconds, and cooling the alloy;
thirdly, putting the mixture into a digital constant-temperature air-blast drying oven at 100 ℃, and raising the temperature to 180 ℃ at the speed of 12 ℃/h;
fourthly, transferring the alloy into deionized water at 0 to 5 ℃ within 3 seconds, and cooling the alloy;
fifthly, putting the materials into a 60 ℃ digital constant temperature air blast drying box, and raising the temperature to 80 ℃ at the speed of 12 ℃/h;
sixthly, transferring the alloy into deionized water at 0 to 5 ℃ within 3 seconds, and cooling the alloy;
seventhly, putting the mixture into a 60 ℃ digital constant-temperature air-blast drying oven, and raising the temperature to 80 ℃ at the speed of 12 ℃/h;
and eighthly, transferring the aluminum alloy into deionized water at 0 to 5 ℃ within 3 s, and cooling the alloy to obtain the heat-treated aluminum alloy.
The aluminum alloy had a surface hardness of 208.4 HV, a tensile strength of 476 MPa, and an elongation of 10.4%. As shown in FIG. 7, the depth of intergranular corrosion of the aluminum alloy was 31 μm. As shown in fig. 8, the 7xxx series ratio of example 7 is such that the intra-grain precipitated phase is mainly a fine and uniform η' phase, the alloy hardness and strength are greatly improved, and the grain boundary precipitated phase is mainly an intermittently distributed η phase, which can inhibit the progress of corrosion.
Claims (8)
1. An intermittent non-isothermal aging treatment process for aluminum alloy, which is applicable to aging-strengthened aluminum alloy, and is characterized in that: the process comprises the following steps:
step one, solution treatment; placing the aluminum alloy at the temperature of 450-560 ℃ for a period of time until most of the components of the aluminum alloy are dissolved in the matrix, thereby forming a supersaturated solid solution;
step two, quenching treatment; transferring the aluminum alloy into a proper fluid to quickly cool the aluminum alloy to room temperature and inhibit the precipitation of components in a supersaturated solid solution;
thirdly, carrying out primary non-isothermal aging treatment; placing the aluminum alloy at the Ta temperature of the traditional artificial aging treatment, and increasing the temperature from the Ta temperature to the Tb temperature at the va rate;
step four, quenching treatment; transferring the aluminum alloy into a suitable fluid to rapidly cool the aluminum alloy to room temperature;
fifthly, secondary non-isothermal aging treatment; placing the aluminum alloy at the Tc temperature, and increasing the temperature from the Tc temperature to the Td temperature at the vb rate;
sixthly, quenching treatment; transferring the aluminum alloy into a proper fluid to rapidly cool the aluminum alloy to room temperature to obtain a heat-treated aluminum alloy;
the Ta temperature of the traditional artificial aging treatment is within the range of 100-190 ℃, the Tb temperature is within the range of 200-380 ℃, the Tc temperature is less than 190 ℃, the Td temperature is less than 380 ℃, and the temperature rise rates of va and vb are within the range of 3-30 ℃/h.
2. The interrupted non-isothermal aging treatment process of the aluminum alloy according to claim 1, characterized in that: the transfer time of the quenching treatment in the second step, the fourth step and the sixth step is not more than 15 s.
3. The interrupted non-isothermal aging treatment process of the aluminum alloy according to claim 1, characterized in that: the fluid of the quenching treatment in the second step, the fourth step and the sixth step is water or polymer organic quenching liquid.
4. The interrupted non-isothermal aging treatment process of the aluminum alloy according to claim 1, characterized in that: the third step of the step is that the primary non-isothermal ageing treatment is incomplete ageing treatment.
5. The interrupted non-isothermal aging treatment process of the aluminum alloy according to claim 1, characterized in that: in the third step, in the first-stage non-isothermal aging treatment, the Tb temperature is less than 2 multiplied by Ta temperature.
6. The interrupted non-isothermal aging treatment process of the aluminum alloy according to claim 1, characterized in that: in the fifth step of the secondary non-isothermal aging treatment, the Tc temperature is lower than the Ta temperature of the traditional artificial aging treatment.
7. The interrupted non-isothermal aging treatment process of the aluminum alloy according to claim 1, characterized in that: in the fifth step of the secondary non-isothermal aging treatment, the Td temperature is <2 × Tc temperature.
8. The interrupted non-isothermal aging treatment process of the aluminum alloy according to the claim 1, characterized in that: if the heat-treated aluminum alloy obtained in the sixth step is in an incompletely aged state, repeating the fifth step and the sixth step after the sixth step for a plurality of times until the heat-treated aluminum alloy reaches a completely aged state.
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Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20070267113A1 (en) * | 2006-03-13 | 2007-11-22 | Staley James T | Method and process of non-isothermal aging for aluminum alloys |
| CN102400068A (en) * | 2011-11-22 | 2012-04-04 | 中国航空工业集团公司北京航空材料研究院 | Non-isothermal aging (NIA) process of 7XXX aluminum alloy |
| CN109207888A (en) * | 2018-09-27 | 2019-01-15 | 西北工业大学 | A kind of efficient creep age forming method of Al-Zn-Mg-Cu aluminum alloy plate non-isothermal |
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Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20070267113A1 (en) * | 2006-03-13 | 2007-11-22 | Staley James T | Method and process of non-isothermal aging for aluminum alloys |
| CN102400068A (en) * | 2011-11-22 | 2012-04-04 | 中国航空工业集团公司北京航空材料研究院 | Non-isothermal aging (NIA) process of 7XXX aluminum alloy |
| CN109207888A (en) * | 2018-09-27 | 2019-01-15 | 西北工业大学 | A kind of efficient creep age forming method of Al-Zn-Mg-Cu aluminum alloy plate non-isothermal |
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