CN102433522A - Grading aging heat treatment method for A356 alloy - Google Patents
Grading aging heat treatment method for A356 alloy Download PDFInfo
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- CN102433522A CN102433522A CN2011103939944A CN201110393994A CN102433522A CN 102433522 A CN102433522 A CN 102433522A CN 2011103939944 A CN2011103939944 A CN 2011103939944A CN 201110393994 A CN201110393994 A CN 201110393994A CN 102433522 A CN102433522 A CN 102433522A
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Abstract
The invention discloses a grading aging heat treatment method for A356 alloy. The heat treatment method comprises links such as high-temperature sold dissolution, natural aging, low-temperature preageing, furnace discharge and air cooling after high-temperature final ageing and the like and concretely comprises the steps that: (1) samples are subjected to heat preservation for 4 to 6 hours at 545 to 555 DEG C and are then quenched at 60 DEG C; (2) the samples are then put for 12 to 36 hours at the room temperature environment; and then, the samples are subjected to the furnace discharge and air cooling after the heat preservation for 4 to 6 hours at 80 to 120 DEG C; and (3) the samples are then subjected to the furnace discharge and air cooling after the heat preservation for 2 to 4 hours at 160 to 170 DEG C. Compared with the traditional solid solution aging process, the heat treatment method has the advantages that the hardness of the A356 aluminium alloy treated by the process is not obviously changed, and the tensile strength can be properly improved. The elongation rate is obviously improved, the improvement range can be stabilized at about 50 percent, in addition, the impact toughness improvement effect is particularly obvious, and the image toughness can be stably improved by more than one time.
Description
Technical field
The present invention relates to a kind of interrupted aging heat treating method of the A356 of being used for alloy.
Background technology
Duraluminum is the second largest structural metallic materials that is only second to ferrous materials.Unique advantages such as compare with ferrous materials, duraluminum has light specific gravity, and height ratio is strong have other structural metallic materials incomparable advantage in automobile " loss of weight, energy-conservation and reduction of discharging ".But the absolute strength of duraluminum is relatively low, and the comprehensive mechanical property such as intensity, toughness that how further to improve duraluminum is very key for applying of duraluminum.Utilizing the high-strong toughness duraluminum of alloyage process development of new is one of important approach.In addition, most of duraluminum can through thermal treatment control with change its matrix, thereby particularly can obtain the mechanical property that timeliness precipitated phase that disperse distributes improves duraluminum.
The heat treatment reinforcement method of duraluminum is at first carried out behind the high temperature solid solution chilling usually and was obtained supersaturation and hold body admittedly, then super saturated solid solution is incubated ageing treatment.In the ageing treatment process, the supersaturation principle gradually aluminum substrate { 10 0} crystal face enrichments form supersaturation atom enrichment region, are commonly referred to GP [I], and at this moment, the lattice distortion of aluminium parent phase hinders dislocation motion, and hardness, intensity raise.Along with the prolongation gradually of soaking time, GP [I] district constantly increases and ordering, and atom is arranged according to certain rules, forms GP [II] district.{ obstruction of dislocation motion is bigger for 10 0} crystal face coherences, the bigger distortion of matrix generation on every side, and strengthening effect improves with parent phase in GP [II] district.And along with the supersaturation atom is distinguished further enrichment at GP [II]; Form the transition phase of some intermetallic compounds; This moment, excessively mutually still { 10 0} crystal face coherences, and reach maximum in this its hardness of starting stage that excessively forms mutually were called " peak timeliness " stage again with parent phase.And along with excessive phase increases gradually, the coherence relation is destroyed, and coherence becomes local coherence fully, and hardness begins to descend---" overaging ".
In the aging thermal treating process of duraluminum, each parameter is bigger to final Effect on Performance, and its heat treatment parameter of different types of alloys differs bigger.Publication number is that the Chinese patent of 1680616A discloses a kind of thermal treatment process of improving the ultra-high-strength aluminum alloy obdurability; This patent has been invented 40～80 ℃ of TRs are carried out in 100～140 ℃ of insulations of a kind of first high-temperature aging again after 30～120 minutes low temperature aging processing to 7055 ultra-high-strength aluminum alloys (Al-Zn-Mg-Cu-Zr).This technology can further promote its toughness when keeping obdurability.Publication number is the thermal treatment process that the Chinese patent of 101117679A has been invented a kind of high-performance aluminum silicon alloy material and piston thereof; Its Si content of its alloy is 12～13%; And contain alloying elements such as more and Cu, Ni, Mg; And a kind of two-stage aging thermal treating process of 250 ℃ * 4～5 hours of 170 ℃ * 6 hours+insulation that is suitable for this alloy is disclosed, have higher high-temperature behavior after this alloy and the thermal treatment thereof.
In numerous duraluminum trades mark, the A356 alloy is a kind of alloy material of common production automotive hub, and its composition range is approximately 6.5～7.5%Si, 0.3～0.5%Mg; All the other are aluminium; This alloy is a hypoeutectic Al-Si alloy, is equivalent to domestic trade mark ZL101A, and its characteristics are that castability is better; Corrosion resistance nature is preferable, and comprehensive mechanical property is higher.But as the wheel hub material, unstable properties after the ubiquity thermal treatment, impelling strength remain practical problemss such as further raising.The conventional thermal treatment worker technology of A356 alloy is that the T6 of GB regulation handles, i.e. solid solution: 535 ± 5 ℃, 6～12 hours, timeliness: room temperature is no less than 8 hours, 180 ± 5 ℃ again, and 3～8 hours.To the A356 duraluminum, publication number is the solid solution aging technique that the Chinese patent of 1999779A openly is used for this alloy, i.e. 550～560 ℃ of insulations of solid solution 99～300 minutes; 140～155 ℃ of insulations of timeliness 99～300 minutes; Compare with GB, its treatment time is shorter relatively and cut down the consumption of energy and cost; But compare with ordinary process, its performance does not have obvious improvement.Application publication number is that the Chinese patent of 101880844A discloses a kind of in short-term thermal treatment process close with Chinese patent 1999779A, i.e. 525～550 ℃ of insulations of solid solution 60～120 minutes, 165～180 ℃ of insulations of timeliness 90～180 minutes.This technology is compared with common T6 technology, and its heat treatment time can shorten one times, and it is organized still and can reach requirement.Publication number is the step aging technology that the Chinese patent of 101638759A discloses a kind of A356 aluminum-alloy wheel, i.e. solid solution: 540 ± 5 ℃, 250～290 minutes, elementary timeliness: 130 ± 5 ℃, 60～90 minutes, timeliness was 170～200 ℃ again, 60～80 minutes.The disclosed heat treatment technics of this patent is compared with traditional technology, and its performance has clear improvement, but toughness is good inadequately.
Summary of the invention
The object of the present invention is to provide a kind of A356 of raising duraluminum comprehensive mechanical property, particularly can significantly improve its flexible heat treating method.The inventive method carries out the seasoning of A356 Aluminium Alloy Solution Treatment through appropriate time to carry out the multistage aging thermal treatment process that the high temperature terminal hour is imitated processing again behind the low temperature preageing then.The present invention is based on the ultimate principle of duraluminum timeliness phase precipitation process; Form high-density GP district in the low temperature preageing stage; Can be terminal hour and imitate stage strengthening phase enough forming core substrates provided herein; Thereby obtain timeliness precipitated phase even, tiny, that disperse distributes, and improve its mechanical property, particularly its toughness.
The object of the invention is realized through following technical scheme:
Be realization the present invention, and guarantee the composition consistence of all laboratory samples, all laboratory samples in the implementation process of the present invention are all taken from same A356 ingot casting.After the ingot casting sampling, directly heat-treat, be processed into the tension specimen that nominal diameter is 6 mm by GB GB/T2975 respectively then, and the regulation that cuts according to GB/T 2975 of impact specimen cuts.
Heat treated primary process is the link such as air cooling of coming out of the stove after high temperature solid solution, seasoning, low temperature preageing, high temperature terminal hour are imitated.
A kind of interrupted aging heat treating method that is used for the A356 alloy may further comprise the steps:
(1) sample is quenched after 2～6 hours 550～560 ℃ of insulations;
(2) again sample was at room temperature placed 12～36 hours; Then sample is incubated 4～6 hours air coolings of coming out of the stove at 80～120 ℃;
(3) again with sample at 160～170 ℃ of insulations air cooling of coming out of the stove after 2～4 hours.
The said quenching of step (1) is that just sample places 60 ℃ water.
Step (2) and (3) described insulation are carried out in insulation can.
The contriver finds in experimental study, in interrupted aging technology, elementary timeliness be the temperature and time in preageing stage to its performance, particularly the flexible influence is bigger.Analyze theoretically, it is big that lower preageing temperature can effectively be placed in the ag(e)ing process GP head of district, and improve the nucleation rate in GP district, for separating out of follow-up timeliness phase provides competent forming core substrate, thereby assurance timeliness precipitated phase size littler, be more evenly distributed.Based on this, it is lower to the invention provides a kind of preageing temperature, can significantly improve the interrupted aging heat treating method of A356 duraluminum impelling strength.
The present invention with respect to prior art have advantage and beneficial effect:
Compare with traditional solid solution aging technique, the hardness of the A356 duraluminum of art breading of the present invention does not have considerable change, and tensile strength can suitably improve.But can obviously improve through its unit elongation of the A356 of art breading of the present invention alloy, increase rate can be stabilized in about 50%, and particularly remarkable for the improvement effect of impelling strength, can stablize and improve more than 1 times.
Description of drawings
The as-cast metallographic structure of Fig. 1 A356 alloy
The A356 alloy metallographic structure that Fig. 2 handles through common solid solution aging
Fig. 3 A356 alloy metallographic structure that interrupted aging is handled after solid solution.
Embodiment
are before statement practical implementation process of the present invention; At first provide the disclosed technical parameter of Chinese patent that utilizes traditional solid-solution and aging heat treatment process method and 101638759A the A356 duraluminum has been carried out the Comparative Examples of handling, and test its tissue and performance.Need to prove that the purpose of Comparative Examples only is to understand better technical characterstic of the present invention and beneficial effect.
Comparative Examples 1
Present embodiment adopts general T 6 solid solution aging techniques that the A356 duraluminum is handled that are used for of standard, and primary process is with the high-temperature aging processing after placement for some time of sample room temperature after high temperature solid solution is handled.Concrete treatment process is: it is that 535 ℃ common chamber type electric resistance furnace carries out solution treatment that sample is placed temperature, be incubated to be transferred to rapidly after 5 hours that to carry out temperature be 60 ℃ tank quenching; Placing 155 ℃ insulation can to carry out the high temperature terminal hour on sample then imitates processing, is incubated the air cooling of coming out of the stove after 5 hours.
A356 alloy its tissue before and after this Comparative Examples is handled changes as illustrated in fig. 1 and 2.Shown in Figure 1 for the A356 alloy before being untreated, i.e. the metallographic structure of as cast condition.What be net distribution among the figure is eutectic Si phase, and all the other zones are matrix Al phase.After solid solution aging was handled, eutectic Si still was net distribution mutually, but the part fuses and diffusion because of taking place in the solution treatment process, makes it change strip or fine particle shape gradually into by strip.Each item performance index of the A356 alloy of handling through common solid solution aging are: hardness 68 HB, tensile strength 245 MPa, unit elongation 5.2%, impelling strength 4.7 J/cm
2
Comparative Examples 2
Publication number is the step aging heat treatment process that the Chinese patent of 101638759A once disclosed a kind of aluminum alloy wheel of vehicle.Its technological process be solid solution, elementary timeliness and again timeliness spray paint three root phases of baking.Be the different and effect of comparative illustration the present invention with this patent, this Comparative Examples adopts the disclosed processing parameter of the Chinese patent of 101638759A to handle the A356 alloy is contrasted.Need to prove that employed sample is from the sampling of A356 ingot casting in this Comparative Examples, and the Chinese patent of 101638759A is directly to take a sample from aluminum-alloy wheel in implementing.Concrete treatment process is: it is that 540 ℃ common chamber type electric resistance furnace carries out solution treatment that sample is placed temperature, be incubated to be transferred to rapidly after 250 minutes that to carry out temperature be 55 ℃ tank quenching; It is that 130 ℃ insulation can carries out the low temperature preageing and handles that the solution hardening sample is placed temperature, is incubated the air cooling of coming out of the stove after 75 minutes; Placing 175 ℃ insulation can to carry out the high temperature terminal hour on low temperature preageing sample imitates processing, is incubated the air cooling of coming out of the stove after 60 minutes.A356 alloy organizing characteristic is close with Fig. 2 after this Comparative Examples is handled, and wherein eutectic Si mainly shows as the net distribution characteristic mutually, and mainly is strip or fine particle shape.Each item performance index of A356 alloy are after this embodiment handles: hardness 72 HB, tensile strength 256 MPa, unit elongation 6.4%, impelling strength 6 J/cm
2
Comparative Examples 3
The purpose of this Comparative Examples and implementation process thereof are identical with Comparative Examples 2.Concrete art breading technology is: it is that 540 ℃ common chamber type electric resistance furnace carries out solution treatment that sample is placed temperature, be incubated to be transferred to rapidly after 250 minutes that to carry out temperature be 55 ℃ tank quenching; It is that 130 ℃ insulation can carries out the low temperature preageing and handles that the solution hardening sample is placed temperature, is incubated the air cooling of coming out of the stove after 75 minutes; Placing 175 ℃ insulation can to carry out the high temperature terminal hour on low temperature preageing sample imitates processing, is incubated the air cooling of coming out of the stove after 60 minutes.A356 alloy organizing characteristic is close with Fig. 2 after this Comparative Examples is handled, and wherein eutectic Si mainly shows as the net distribution characteristic mutually, and mainly is strip or fine particle shape.Each item performance index are: hardness 69 HB, tensile strength 257 MPa, unit elongation 5.6%, impelling strength 7.3 J/cm
2
for understanding technical characterstic of the present invention better, are further described the present invention below in conjunction with embodiment, need to prove, Comparative Examples and embodiment are not the restriction to protection domain of the present invention.
Embodiment 1
Interrupted aging thermal treatment process after the present embodiment employing solid solution, heat treated primary process are the air cooling of coming out of the stove after high temperature solid solution, seasoning, low temperature preageing, the high temperature terminal hour effect.Concrete treatment process is: it is that 550 ℃ common chamber type electric resistance furnace carries out solution treatment that sample is placed temperature, be incubated to be transferred to rapidly after 6 hours that to carry out temperature be 60 ℃ tank quenching; The solution hardening sample was carried out seasoning in 12 hours in the room temperature environment held; Then sample being placed temperature is that 120 ℃ insulation can carries out the low temperature preageing and handles, and is incubated the air cooling of coming out of the stove after 4 hours; Placing 160 ℃ insulation can to carry out the high temperature terminal hour on low temperature preageing sample imitates processing, is incubated the air cooling of coming out of the stove after 4 hours.It is as shown in Figure 3 that the A356 alloy is handled its metallographic structure through this embodiment, and the tissue signature after its tissue signature and common solid solution aging shown in Figure 2 are handled is close, and eutectic Si mainly shows as the net distribution characteristic mutually, and mainly is strip or fine particle shape.Each item performance index are: hardness 66 HB, tensile strength 260 MPa, unit elongation 7.6%, impelling strength 9.9 J/cm
2
Embodiment 2
Interrupted aging thermal treatment process after the present embodiment employing solid solution, heat treated primary process are the air cooling of coming out of the stove after high temperature solid solution, seasoning, low temperature preageing, the high temperature terminal hour effect.Concrete treatment process is: it is that 560 ℃ common chamber type electric resistance furnace carries out solution treatment that sample is placed temperature, be incubated to be transferred to rapidly after 2 hours that to carry out temperature be 60 ℃ tank quenching; The solution hardening sample was carried out seasoning in 24 hours in the room temperature environment held; Then sample being placed temperature is that 80 ℃ insulation can carries out the low temperature preageing and handles, and is incubated the air cooling of coming out of the stove after 6 hours; Placing 170 ℃ insulation can to carry out the high temperature terminal hour on low temperature preageing sample imitates processing, is incubated the air cooling of coming out of the stove after 2 hours.A356 alloy organizing characteristic and 2 close after this embodiment handles, and each item performance index are: hardness 67 HB, tensile strength 267 MPa, unit elongation 8.9%, impelling strength 11.2 J/cm
2
Embodiment 3
Interrupted aging thermal treatment process after the present embodiment employing solid solution, heat treated primary process are the air cooling of coming out of the stove after high temperature solid solution, seasoning, low temperature preageing, the high temperature terminal hour effect.Concrete treatment process is: it is that 555 ℃ common chamber type electric resistance furnace carries out solution treatment that sample is placed temperature, be incubated to be transferred to rapidly after 3 hours that to carry out temperature be 60 ℃ tank quenching; The solution hardening sample was carried out seasoning in 36 hours in the room temperature environment held; Then sample being placed temperature is that 100 ℃ insulation can carries out the low temperature preageing and handles, and is incubated the air cooling of coming out of the stove after 5 hours; Placing 165 ℃ insulation can to carry out the high temperature terminal hour on low temperature preageing sample imitates processing, is incubated the air cooling of coming out of the stove after 3 hours.A356 alloy organizing characteristic and 2 close after this embodiment handles, and each item performance index are: hardness 72 HB, tensile strength 286 MPa, unit elongation 7.8%, impelling strength 9.6 J/cm
2
for ease of directly contrasting the performance data of Comparative Examples and alloy that embodiment handles, table 1 has provided corresponding hardness, tensile strength, unit elongation and impelling strength.
Can know that from table 1 each item performance handle the hardness of alloy performance through Comparative Examples and embodiment and do not have noticeable change, its numerical value is between 68～72HB.And see that from tensile strength compare with common solid solution aging technique (Comparative Examples 1), the intensity of Comparative Examples 2 and 3 alloys of handling has suitable raising; But increase rate is limited, be merely about 5%, and for embodiment 1 to 3; Its intensity is compared further raising with Comparative Examples 2 with 3; Compare with traditional technology, the increase rate of embodiment 1 to 3 is respectively 6%, 9% and 16%, and the increase rate of embodiment 3 is maximum.
For unit elongation, to compare with common solid solution aging technique (Comparative Examples 1), the unit elongation of Comparative Examples 2 and 3 alloys of handling has suitable raising, and increase rate is respectively 23% and 8%.And for embodiment 1 to 3, its unit elongation is compared further raising with Comparative Examples 2 with 3.Compare with traditional technology, the unit elongation increase rate of embodiment 1 to 3 alloy of handling is respectively 46%, 71% and 50%, and wherein the increase rate of embodiment 2 is the most remarkable.
For impelling strength, to compare with common solid solution aging technique (Comparative Examples 1), the impelling strength of Comparative Examples 2 and 3 alloys of handling has suitable raising, and increase rate is respectively 28% and 55%.And for embodiment 1 to 3, its unit elongation is compared further raising with Comparative Examples 2 with 3.Compare with traditional technology, the unit elongation increase rate of embodiment 1 to 3 alloy of handling is respectively 111%, 104% and 138%, and obviously impelling strength can be stablized raising more than 1 times.
Can find out that from the performance data of Comparative Examples and embodiment different solid solution aging techniques does not have obvious influence to A356 hardness of alloy performance, but tensile strength, unit elongation and impelling strength are had improvement effect in various degree.Compare with traditional solid solution aging technique, its performance of A356 duraluminum of utilizing the disclosed technical parameter of Chinese patent of 101638759A to handle improves.And for the handled A356 alloy of the present invention; Its performance has further to be improved, and particularly the increase rate of its unit elongation and impelling strength is bigger, compares with traditional technology; The increase rate of unit elongation can be stabilized in about 50%, improves more than 1 times and impelling strength is stable.
Table 1 Comparative Examples and embodiment handle the mechanical property of A356 alloy
| ? | Hardness (HB) | Tensile strength (MPa) | Unit elongation (%) | Impelling strength (J/cm 2) |
| Comparative Examples 1 | 68 | 245 | 5.2 | 4.7 |
| Comparative Examples 2 | 72 | 256 | 6.4 | 6 |
| Comparative Examples 3 | 69 | 257 | 5.6 | 7.3 |
| Embodiment 1 | 68 | 260 | 7.6 | 9.9 |
| Embodiment 2 | 67 | 267 | 8.9 | 11.2 |
| Embodiment 3 | 72 | 286 | 7.8 | 9.6 |
Claims (3)
1. an interrupted aging heat treating method that is used for the A356 alloy is characterized in that, may further comprise the steps:
(1) sample is quenched after 2～6 hours 550～560 ℃ of insulations;
(2) again sample was at room temperature placed 12～36 hours; Then sample is incubated 4～6 hours air coolings of coming out of the stove at 80～120 ℃;
(3) again with sample at 160～170 ℃ of insulations air cooling of coming out of the stove after 2～4 hours.
2. interrupted aging heat treating method according to claim 1 is characterized in that, the said quenching of step (1) is that just sample places 60 ℃ water.
3. interrupted aging heat treating method according to claim 1 is characterized in that, step (2) and (3) described insulation are carried out in insulation can.
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN102796974A (en) * | 2012-08-13 | 2012-11-28 | 北京有色金属研究总院 | Improved 7000 series aluminum alloy double-stage overaging heat treatment technology |
| CN102839338A (en) * | 2012-09-27 | 2012-12-26 | 辽宁忠旺集团有限公司 | Aging technology for optimizing weldability of aluminum alloy A7N01-T5 |
| CN104762536A (en) * | 2015-02-02 | 2015-07-08 | 安徽省斯特嘉汽车零部件有限公司 | Preparation method of magnesium borate whisker-reinforced A356 aluminum alloy wheel hub |
| CN114277324A (en) * | 2022-01-06 | 2022-04-05 | 国家高速列车青岛技术创新中心 | Heat treatment method of ZL101A aluminum alloy for resisting marine environment corrosion |
| CN115181922A (en) * | 2022-05-20 | 2022-10-14 | 上海交通大学 | Intermediate temperature heat treatment process for die-casting Al-Si-Mg series alloy |
| CN115612951A (en) * | 2022-10-27 | 2023-01-17 | 大亚车轮制造有限公司 | Double-stage aging heat treatment method for aluminum alloy wheel |
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102796974A (en) * | 2012-08-13 | 2012-11-28 | 北京有色金属研究总院 | Improved 7000 series aluminum alloy double-stage overaging heat treatment technology |
| CN102839338A (en) * | 2012-09-27 | 2012-12-26 | 辽宁忠旺集团有限公司 | Aging technology for optimizing weldability of aluminum alloy A7N01-T5 |
| CN104762536A (en) * | 2015-02-02 | 2015-07-08 | 安徽省斯特嘉汽车零部件有限公司 | Preparation method of magnesium borate whisker-reinforced A356 aluminum alloy wheel hub |
| CN114277324A (en) * | 2022-01-06 | 2022-04-05 | 国家高速列车青岛技术创新中心 | Heat treatment method of ZL101A aluminum alloy for resisting marine environment corrosion |
| CN114277324B (en) * | 2022-01-06 | 2023-03-10 | 国家高速列车青岛技术创新中心 | Heat treatment method of ZL101A aluminum alloy for marine environment corrosion resistance |
| CN115181922A (en) * | 2022-05-20 | 2022-10-14 | 上海交通大学 | Intermediate temperature heat treatment process for die-casting Al-Si-Mg series alloy |
| CN115612951A (en) * | 2022-10-27 | 2023-01-17 | 大亚车轮制造有限公司 | Double-stage aging heat treatment method for aluminum alloy wheel |
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