CN102586706B - A kind of heat treating method making aluminium alloy obtain high-dimensional stability - Google Patents
A kind of heat treating method making aluminium alloy obtain high-dimensional stability Download PDFInfo
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- CN102586706B CN102586706B CN201210056797.8A CN201210056797A CN102586706B CN 102586706 B CN102586706 B CN 102586706B CN 201210056797 A CN201210056797 A CN 201210056797A CN 102586706 B CN102586706 B CN 102586706B
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- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 39
- 238000000034 method Methods 0.000 title claims abstract description 39
- 230000032683 aging Effects 0.000 claims abstract description 19
- 239000000956 alloy Substances 0.000 claims description 15
- 238000010438 heat treatment Methods 0.000 claims description 14
- 229910045601 alloy Inorganic materials 0.000 claims description 9
- 229910017818 Cu—Mg Inorganic materials 0.000 claims description 8
- 238000001556 precipitation Methods 0.000 claims description 3
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 2
- 239000011159 matrix material Substances 0.000 claims description 2
- 229910052710 silicon Inorganic materials 0.000 claims description 2
- 239000010703 silicon Substances 0.000 claims description 2
- 238000009827 uniform distribution Methods 0.000 claims description 2
- 238000007669 thermal treatment Methods 0.000 abstract description 9
- 230000035882 stress Effects 0.000 abstract description 2
- 239000012071 phase Substances 0.000 description 28
- 239000000523 sample Substances 0.000 description 20
- 238000012360 testing method Methods 0.000 description 12
- 238000005266 casting Methods 0.000 description 5
- 238000005382 thermal cycling Methods 0.000 description 4
- 238000005275 alloying Methods 0.000 description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 3
- 229910052782 aluminium Inorganic materials 0.000 description 3
- 239000004411 aluminium Substances 0.000 description 3
- 238000004364 calculation method Methods 0.000 description 3
- 239000000470 constituent Substances 0.000 description 3
- 238000001816 cooling Methods 0.000 description 3
- 238000009413 insulation Methods 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 238000013112 stability test Methods 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 2
- 238000003754 machining Methods 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000013016 damping Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 239000008384 inner phase Substances 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
Landscapes
- Heat Treatment Of Articles (AREA)
- Cylinder Crankcases Of Internal Combustion Engines (AREA)
Abstract
The present invention relates to a kind of heat treating method making aluminium alloy obtain high-dimensional stability, it is characterized in that: in aluminum alloy heat treating processes, apply 175-185 DEG C of timeliness and 245-255 DEG C of overaging two kinds of aging treatment process simultaneously; Be 490-500 DEG C completing temperature, time is after the solution treatment of 0.5-6 hour, carries out ageing treatment, and the heat treating method that the present invention states can be applied under applied at elevated temperature condition, have high dimension stability require, the thermal treatment of automobile dynamic system part.Described heat treating method can guarantee that aluminium alloy is below 250 DEG C, has good dimensional stability under life-time service condition, and without under applied stress condition, the tension set of part is not more than 0.05%.
Description
Technical field
The present invention relates to a kind of heat treating method making aluminium alloy obtain high-dimensional stability, particularly relate to a kind of thermal treatment process for automobile dynamic system Al-Si-Cu-Mg alloy, ensure that aluminum alloy part is in high temperature (≤250 DEG C particular by specific thermal treatment process) there is good dimensional stability under working conditions.
Background technology
Aluminium alloy is a kind of low-density structural metallic materials, its specific tenacity, specific modulus are high, machining property is excellent, there is good corrosion resisting property, excellent damping property and machinability, and certain impact shock load can be born, adopt aluminium alloy can reduce the deadweight of product, reduce machining energy, reduce energy consumption.Along with the requirement of automotive light weight technology and energy-conserving and environment-protective, aluminum alloy casting is widely used in automotive industry, and for engine cylinder-body, the manufacture of the important vital part such as cylinder cap.But aluminum alloy part in thermal treatment and applied at elevated temperature process often along with dimensional change, the factor of dimensional change is caused to mainly contain two aspects, the first raises the thermal expansion caused due to temperature, and it two is size distortions that in use procedure, precipitated phase causes.The distortion of first part gets back to initial temperature along with foundry goods, its dimensional change can disappear, the size distortion of second section causes due to the inner phase transformation of alloy, even the initial temperature of getting back to, this portion deforms also cannot completely dissolve, form tension set, and along with the increase of times of thermal cycle, this portion deforms also can change.Produce tension set in aluminum alloy part use procedure, the dimensional change of the part (such as inlay the parts such as cylinder sleeve and produce distortion) be mated will be had influence on, thus have influence on overall task performance.Therefore the tension set of aluminum alloy part under thermal cycling working conditions is the producer of aluminum alloy part and the problem of application person's concern always.
The Al-Si-Cu-Mg alloy major cause producing size tension set that works under the high temperature conditions is owing to working under the high temperature conditions for a long time, precipitated phase is there will be in aluminium alloy micostructure, specific volume and the α-Al of precipitated phase there are differences, thus cause aluminium alloy part in use to produce the tension set of extending or shrinking.With regard to Al-Si-Cu-Mg alloy system, long term operation under≤250 DEG C of conditions, Si phase is comparatively stable, causes the precipitated phase mainly as shown in table 1 of dimensional change, because the Precipitation Temperature of each precipitated phase is different, also there is phase co-conversion each other.If thus carry out artificial aging at the same temperature, the phase in version of precipitated phase is incomplete, thus causes precipitated phase under applied at elevated temperature condition subsequently to continue to produce phase in version, thus causes the tension set of aluminum alloy part.
Summary of the invention
The object of the present invention is to provide a kind of heat treating method making aluminium alloy obtain high-dimensional stability, can be applicable to the thermal treatment of automobile dynamic system Al-Si-Cu-Mg alloy-steel casting.The dimensional stability of aluminium alloy in elevated temperature thermal cycles process is realized by the mode of alternating temperature ageing treatment, make in aluminium alloy micostructure, containing the stable particulate state precipitated phase being of a size of 0.2-3 μm in a large number, such that the dimensional stability of material monolithic is high is provided with good microstructure basis.
Technical scheme of the present invention is achieved in that a kind of heat treating method making aluminium alloy obtain high-dimensional stability, it is characterized in that concrete heat treatment process is as follows: in aluminum alloy heat treating processes, apply 175-185 DEG C of timeliness and 245-255 DEG C of overaging two kinds of aging treatment process simultaneously; Be 490-500 DEG C completing temperature, the time is after the solution treatment of 0.5-6 hour, and it is as follows to carry out its process of ageing treatment, and first time is ageing treatment, treatment temp: 175-185 DEG C, time: 2/3-1 hour; Second time is Wetted constructures, treatment temp: 245-255 DEG C, time: 2/3-1 hour; Third time is ageing treatment, treatment temp: 175-185 DEG C, time: 1-3 hour; By above ageing process, first make precipitated phase separate out, then adopt Wetted constructures technique to make precipitated phase precipitation process complete, finally by aging treatment process, precipitated phase in alloy microscopic structure is stablized, and change θ into
,phase (Al
4cu
2), S
,phase (Al
2and a small amount of θ phase (Al CuMg)
8cu
4) and θ
,phase (Al
6cu
2).
Described aluminium alloy, its alloy system is Al-Si-Cu-Mg system alloy, and microstructure is after heat treatment the particulate state precipitated phase being uniform-distribution with silicon phase He being of a size of 0.2-3 μm in α-Al matrix.
Solution treatment in described heat treating method, timeliness and Wetted constructures time can adjust within the time of statement according to the thickness of part, but can not be less than minimum time requirement.
Positively effect of the present invention may be used for the thermal treatment that automobile dynamic system part etc. needs to have the aluminum alloy casting that high temperature dimensional stability requires, described heat treating method can guarantee that aluminium alloy works long hours under condition and has good dimensional stability below 250 DEG C, and it is not more than 0.05% without tension set under applied stress condition.(correlation properties of precipitated phase are as shown in table 1).
precipitated phase in table 1 Al-Si-Cu-Mg system alloy and relevant parameter.
| Sequence number | Precipitated phase | Composition | Cu content Wt% | Mg content Wt% | Specific volume (cm 3/ g） |
| 1 | θ | Al 8Cu 4 | 54.2 | - | 0.2299 |
| 2 | θ , | Al 4Cu 2 | 54.2 | - | 0.2427 |
| 3 | θ , , | Al 6Cu 2 | 44.0 | - | 0.2611 |
| 4 | S , | Al 2CuMg | 44.8 | 17.1 | 0.2817 |
Accompanying drawing explanation
Fig. 1 is aluminum alloy materials metallographic structure after heat treatment in embodiment 1.
Fig. 2 is the scanned photograph of aluminum alloy materials precipitated phase after heat treatment in embodiment 1.
Fig. 3 is aluminum alloy materials material tension set test result after 3 elevated temperature thermal cycles in embodiment 1.
Fig. 4 is aluminum alloy materials metallographic structure after heat treatment in embodiment 2.
Fig. 5 is the scanned photograph of aluminum alloy materials precipitated phase after heat treatment in embodiment 2.
Fig. 6 is aluminum alloy materials material tension set test result after 3 elevated temperature thermal cycles in embodiment 2.
Embodiment
Below in conjunction with drawings and Examples, the present invention will be further described:
Embodiment 1
Aluminium alloy engine cylinder block casting, alloying constituent: Si:6.5 Cu: 3.5 Mn:0.35 Mg:0.55 all the other be aluminium, part average wall thickness 3.5mm.
Thermal treatment process is:
Solid solution temperature: 495 ± 2 DEG C, the time: 3 hours;
Artificial aging process
For the first time, temperature: 175 DEG C, the time: 2/3 hour;
For the second time, temperature: 245 DEG C, the time: 1 hour;
For the third time, temperature: 175 DEG C, the time: 1 hour;
Dimensional stability test sample is cut by cast-internal, is of a size of φ 5 × 25.Elevated temperature thermal cycles probe temperature is 250 DEG C, and test condition is: be heated to 250 DEG C by room temperature, rate of heating 10 DEG C/min, and insulation 5h, is cooled to room temperature, speed of cooling 10 DEG C/min, incubated at room temperature 1h, measures the tension set of sample.Repeat above-mentioned test process, carry out 3 thermal cyclings altogether.Be averaged with 5 test sample results, the set deformation volume of calculation sample.After heat treatment its metallographic structure and precipitated phase are as depicted in figs. 1 and 2, and as shown in Figure 3, the set deformation volume of visible sample is less than 0.05% to the set deformation volume of sample.
Embodiment 2
Aluminium alloy engine cylinder block casting, alloying constituent: Si:6.0 Cu: 3.2 Mn:0.35 Mg:0.55 all the other be aluminium, part average wall thickness 4.0 mm.
Thermal treatment process is:
Solid solution temperature: 495 ± 5 DEG C, the time: 3.5 hours;
Artificial aging process
For the first time, temperature: 185 DEG C, the time: 2/3 hour;
For the second time, temperature: 255 DEG C, the time: 1 hour;
For the third time, temperature: 185 DEG C, the time: 2.5 hours;
Dimensional stability test sample is cut by cast-internal, is of a size of φ 5 × 25.Elevated temperature thermal cycles probe temperature is 250 DEG C, and test condition is: be heated to 180 DEG C by room temperature, rate of heating 10 DEG C/min, and insulation 5h, is cooled to room temperature, speed of cooling 10 DEG C/min, incubated at room temperature 1h, measures the tension set of sample.Repeat above-mentioned test process, carry out 3 thermal cyclings altogether.Be averaged with 5 test sample results, the set deformation volume of calculation sample.After heat treatment its metallographic structure and precipitated phase are as shown in Figure 4 and Figure 6, the set deformation volume of sample as shown in Figure 6, the set deformation volume of visible sample much smaller than 0.05%, near 0.03%.
Embodiment 3
Aluminium alloy engine machine bracket, alloying constituent: Si:6.1 Cu: 3.8 Mn:0.26 Mg:0.35 all the other be aluminium, part average wall thickness 4.2 mm, thickest 8.0mm.
Thermal treatment process is:
Solid solution temperature: 490 ± 5 DEG C, the time: 4.5 hours;
Artificial aging process
For the first time, temperature: 180 DEG C, the time: 1 hour;
For the second time, temperature: 250 DEG C, the time: 1 hour;
For the third time, temperature: 180 DEG C, the time: 3 hours;
Dimensional stability test sample is cut by cast-internal, is of a size of φ 5 × 25.Elevated temperature thermal cycles probe temperature is 250 DEG C, and test condition is: be heated to 180 DEG C by room temperature, rate of heating 10 DEG C/min, and insulation 5h, is cooled to room temperature, speed of cooling 10 DEG C/min, incubated at room temperature 1h, measures the tension set of sample.Repeat above-mentioned test process, carry out 3 thermal cyclings altogether.Be averaged with 5 test sample results, the set deformation volume of calculation sample, test sample set deformation volume is not more than 0.05%.
Claims (3)
1. make aluminium alloy obtain a heat treating method for high-dimensional stability, it is characterized in that concrete heat treatment process is as follows: in cast aluminium alloy Al-Si-Cu-Mg heat treatment process, apply 175-185 DEG C of timeliness and 245-255 DEG C of overaging two kinds of aging treatment process simultaneously; Be 490-500 DEG C completing temperature, the time is after the solution treatment of 0.5-6 hour, and it is as follows to carry out its process of ageing treatment, and first time is ageing treatment, treatment temp: 175-185 DEG C, time: 2/3-1 hour; Second time is Wetted constructures, treatment temp: 245-255 DEG C, time: 2/3-1 hour; Third time is ageing treatment, treatment temp: 175-185 DEG C, time: 1-3 hour; By above ageing process, first make precipitated phase separate out, then adopt Wetted constructures technique to make precipitated phase precipitation process complete, finally by aging treatment process, precipitated phase in alloy microscopic structure is stablized, and change θ into
,phase Al
4cu
2, S
,phase Al
2cuMg and a small amount of θ phase Al
8cu
4and θ
,phase Al
6cu
2.
2. a kind of heat treating method making aluminium alloy obtain high-dimensional stability according to claim 1, it is characterized in that the solution treatment in described heat treating method, timeliness and Wetted constructures time can adjust within the time of statement according to the thickness of part, but can not be less than minimum time requirement.
3. a kind of heat treating method making aluminium alloy obtain high-dimensional stability according to claim 1, it is characterized in that described cast aluminium alloy Al-Si-Cu-Mg, microstructure is after heat treatment the particulate state precipitated phase being uniform-distribution with silicon phase He being of a size of 0.2-3 μm in α-Al matrix.
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| CN201210056797.8A CN102586706B (en) | 2012-03-07 | 2012-03-07 | A kind of heat treating method making aluminium alloy obtain high-dimensional stability |
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|---|---|---|---|
| CN201210056797.8A CN102586706B (en) | 2012-03-07 | 2012-03-07 | A kind of heat treating method making aluminium alloy obtain high-dimensional stability |
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| CN102586706B true CN102586706B (en) | 2015-10-14 |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| WO2007111325A1 (en) * | 2006-03-28 | 2007-10-04 | Showa Denko K.K. | Process for production of liner-constituting members |
| CN100557053C (en) * | 2006-12-19 | 2009-11-04 | 中南大学 | High-strength, high-toughness, corrosion-resistant Al-Zn-Mg-(Cu) alloy |
| CN102108463B (en) * | 2010-01-29 | 2012-09-05 | 北京有色金属研究总院 | Aluminium alloy product suitable for manufacturing structures and preparation method |
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Effective date of registration: 20200628 Address after: 130011 No.1, xinhongqi street, Changchun automobile economic and Technological Development Zone, Jilin Province Co-patentee after: FAW FOUNDRY Co.,Ltd. Patentee after: CHINA FIRST AUTOMOBILE WORKS GROUP Co.,Ltd. Address before: 130011 No. 2259 Dongfeng Avenue, Xi Xin Economic and Technological Development Zone, Jilin, Changchun Patentee before: CHINA FIRST AUTOMOBILE WORKS GROUP Co.,Ltd. |