CN105568082A - Heat treatment method for Al-Si-Cu-Mg casting alloy - Google Patents
Heat treatment method for Al-Si-Cu-Mg casting alloy Download PDFInfo
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- CN105568082A CN105568082A CN201610070598.0A CN201610070598A CN105568082A CN 105568082 A CN105568082 A CN 105568082A CN 201610070598 A CN201610070598 A CN 201610070598A CN 105568082 A CN105568082 A CN 105568082A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
Abstract
The invention relates to Al-Si-Cu-Mg casting alloy. The Al-Si-Cu-Mg casting alloy is formed by smelting electrolytic aluminum, silicon metal, pure magnesium and Al-Cu intermediate alloy and comprises, by weight, 5.5%-6.5% of Si, 1.8%-2.2% of Cu, 0.45%-0.55% of Mg and the balance Al, and the ratio of the Cu to the Mg is 4:1. The Al-Si-Cu-Mg casting alloy is subjected to two-stage solid solution treatment and two-stage aging treatment, it can be ensured that precipitated phases of the Al-Si-Cu-Mg casting alloy are all dissolved in a matrix through suitable solid solution temperature and time, and overburning of crystal boundaries cannot be caused; and then the characteristics and mechanical properties precipitated by the alloy phases are controlled through two-stage aging treatment, so that the tensile property of the Al-Si-Cu-Mg casting alloy obtained through the method is obviously improved in index compared with the tensile property of Al-Si-Cu-Mg casting alloy subjected to T6 treatment.
Description
Technical field
The present invention relates to metallurgical technology field, especially a kind of heat treating method of Al-Si-Cu-Mg casting alloy.
Background technology
Be T6 thermal treatment to the typical heat processing mode of sand mold and gravitational casting Al-Si Alloyapplication used, this heat treatment mode mainly comprises:
1, carry out solution treatment at relatively high temperatures, make the rich Cu of formation, rich Mg phase grain dissolution, obtain the alloying constituent of high uniformity.
2, quench treatment, generally selects room temperature condition to quench, and obtains the supersaturated solid solution in solid solution atom and room.
3, age hardening process, under room temperature (natural aging) or raised temperature (artificial aging) condition, from supersaturated solid solution precipitation strength phase.
The temperature of solution treatment generally selects the eutectic temperature close to alloy, can make like this to be formed in process of setting containing Cu, containing Mg phased soln, make element uniformity in alloy, also make the nodularization of eutectic Si particle.But because Mg and Cu adds in casting Al-Si alloy, the solid solution temperature of alloy depends primarily on the solvent temperature of the precipitated phase formed by Cu and Mg.The solid solubility temperature of as cast condition Al-Si-Mg alloy is typically chosen in 540-550 DEG C, but owing to containing Cu phase when temperature is better, local melting can occur, and the solid solubility temperature of the alloy containing Cu element is general lower.According to the research of Samuel in 1998, in the alloy of the lower A319 of Mg content, starting to dissolve at 519 DEG C containing Cu phase, is in the A319 alloy of 0.5wt.% at Mg content, due to Q-Al
5mg
8si
5cu
2the existence of phase, the solvent temperature containing Cu phase drops to 505 DEG C.Set suitable solid solubility temperature and can avoid alloy generation burn-off phenomenon, but this depends on the solidification rate of alloy and the heating rate of solution treatment.The former affects the volume fraction, size, pattern and the kind that contain Cu phase, and the latter then can affect the dissolution degree containing Cu phase in solution heat process.
For Al-Si-Cu-Mg alloy, in solid solution process, Q phase is grown up and is dissolved the setting depending on alloying constituent and solid solubility temperature.The people such as Lasa and Rodriguez calculate when Cu content controls within the scope of 3.5-4.4wt.%, change Mg content, the volume fraction that Q phase is shared after as cast condition and solution treatment.Research finds, after solution treatment, the area volume mark of Q does not change, and this just illustrates that Q compares stable, and dissolves slower.Correlative study finds, in the alloy of low Cu (1.4wt.%) high Mg (1.3wt.%), in solid solution process, Q meets and replaces undissolved Mg2Si phase, causes Q phase content to increase.The solid solubility temperature of forefathers is generally selected in 490 DEG C, but the solvent temperature of Q phase is at 530 DEG C.In solid solution process, in Al-Si-Cu-Mg alloy phase dissolving and homogenize time used than not short containing the time that the alloy of Mg is used.
At high temperature dissolve owing to meeting containing Cu, therefore, the solid solubility temperature of Al-Si-Cu-Mg alloy can not be too high, but under low temperature, solid solution can not obtain best solid solution result, because concentration and the room of the solid solution atom of solid solution acquisition are at low temperatures all lower, Si particle nodularization effect is also bad.Therefore, in the research of Samuel in 1998, joined by Mg in Al-Si-Cu alloy, after 480 DEG C of solution treatment, the intensity of alloy does not improve, but after solid solubility temperature is elevated to 500 DEG C, the intensity of alloy increases.
Therefore, forefathers' research shows, selects two-stage solution treatment, both can obtain good solid solution effect, save solution time again Al-Si-Cu-Mg quad alloy.In the experiment of the people such as nineteen ninety-five Sokolowski, find that lesser temps 495 DEG C of solid solution 8h are selected in the solid solution of the alloy first step, make containing Cu grain dissolution, then, be elevated to 520 DEG C of solid solution 2h, obtain the alloy of uniform alloy element, this solution treatment mode makes the intensity of alloy and plasticity all to improving.But, if solid solubility temperature is too high, alloy local burning can be caused, the mechanical property of alloy sharply declines, little by little, this contradiction has been upgraded the barrier become in industry, so the parameter such as temperature and time of adopting of the double_stage guide of the ratio chosen for the element of Al-Si-Cu-Mg quad alloy and correspondence thereof and two-stage time effect becomes the main starting point that alloy production person improves the quality of products and saves production cost.
Summary of the invention
The present invention is directed to the deficiencies in the prior art part, provide a kind of cost-saving and have the heat treating method of the Al-Si-Cu-Mg casting alloy of good strength and toughness concurrently.
For achieving the above object, technical scheme of the present invention is:
A kind of Al-Si-Cu-Mg casting alloy, this casting alloy electrolytic aluminum, Pure Silicon Metal, pure magnesium and the melting of Al-Cu master alloy form, its feed composition and weight percent thereof are respectively: Si:5.5 ~ 6.5%, Cu:1.8 ~ 2.2%, Mg:0.45 ~ 0.55%, Fe: be less than 0.15%, Ti:0.10 ~ 0.15%, Mn: be less than 0.05%, Zn: be less than 0.05%, other impurity are less than 0.01%, all the other are Al, and wherein Cu/Mg is than being 4:1.
And feed composition and the weight percent thereof of described Al-Si-Cu-Mg casting alloy are respectively: Si:5.98%, Cu:2.08%, Mg:0.52%, Fe:0.02%, Ti: be less than 0.01%, Mn: be less than 0.01%, Zn: be less than 0.01%, other impurity are less than 0.01%, and all the other are Al.
The heat treating method of above-mentioned Al-Si-Cu-Mg casting alloy is:
(1) double_stage guide process is adopted to described Al-Si-Cu-Mg casting alloy;
(2) to the Al-Si-Cu-Mg casting alloy cooling after double_stage guide process;
(3) two-stage time effect process is adopted to cooled Al-Si-Cu-Mg casting alloy, wherein the temperature of one-level ageing treatment is 180 DEG C, and the treatment time is 6h, and the temperature of secondary time effect process is 100 ~ 200 DEG C, treatment time is 0.5 ~ 2h, completes the thermal treatment of Al-Si-Cu-Mg casting alloy.
And in the double_stage guide process that step is (1) described, the temperature of one-level solution treatment is 470 DEG C, and the treatment time is 6h, and the temperature of secondary solution treatment is 530 DEG C, and the treatment time is 2h.
And the (2) described cooling temperature of step is 18 DEG C, and cooling time is 10s.
And the temperature of the secondary time effect process of the two-stage time effect process that step is (3) described is 200 DEG C, and the treatment time is 5h.
Advantage of the present invention is:
The present invention have employed double_stage guide process and two-stage time effect process to Al-Si-Cu-Mg casting alloy, suitable solid solubility temperature and time can ensure that the precipitated phase of alloy is all dissolved in matrix, crystal boundary burning can not be caused again, then adopt two-stage time effect processing controls feature and the mechanical property of alloy phase precipitation, the tensile property producing the Al-Si-Cu-Mg casting alloy obtained thus comparatively adopts the tensile property of the Al-Si-Cu-Mg casting alloy of T6 process to have obvious index to promote.
The present invention has carried out rational proportioning to the moiety of Al-Si-Cu-Mg casting alloy, double_stage guide process targetedly and two-stage time effect process is have employed for the Al-Si-Cu-Mg casting alloy that this proportioning is corresponding, although be applied in the prior art in the double_stage guide process of this case employing and the treatment process of two-stage time effect process, but this case is all create beyond thought parameter value in research and production process for the double_stage guide process of specific components Al-Si-Cu-Mg casting alloy and two-stage time effect treatment temp and time, or even overcome the technology prejudice of certain art technology, this heat treated mode is not only embodied in theory, but can be widely used in the heat treated industrial production of Al-Si-Cu-Mg casting alloy.
Accompanying drawing explanation
Fig. 1 is the tensile strength of embodiment 1 ~ embodiment 4 correspondence in the present invention and the index contrast figure of unit elongation;
Fig. 2 is the tensile strength of embodiment 5 ~ embodiment 6 correspondence in the present invention and the index contrast figure of unit elongation.
Embodiment:
Below by specific embodiment, the invention will be further described, and following examples are descriptive, is not determinate, can not limit protection scope of the present invention with this.
A kind of Al-Si-Cu-Mg casting alloy, this casting alloy electrolytic aluminum, Pure Silicon Metal, pure magnesium and the melting of Al-Cu master alloy form, and its feed composition and weight percent thereof are respectively: Si:5.5 ~ 6.5%, Cu:1.8 ~ 2.2%, Mg:0.45 ~ 0.55%, Fe: be less than 0.15%, Ti:0.10 ~ 0.15%, Mn: be less than 0.05%, Zn: be less than 0.05%, other impurity are less than 0.01%, and all the other are Al.
In the present invention, in the component of aforementioned proportion, need to keep Cu/Mg than being 4:1, through repeatedly contrasting, Si:5.98%, Cu:2.08%, Mg:0.52%, Fe:0.02%, Ti: be less than 0.01%, Mn: be less than 0.01%, Zn: be less than 0.01%, other impurity are less than 0.01%, and all the other are Al, and the component of this group ratio is best.
To the Al-Si-Cu-Mg casting alloy of above-mentioned preferred proportion, adopt following heat treatment step:
(1) adopt double_stage guide process to Al-Si-Cu-Mg casting alloy, the temperature of one-level solution treatment is 470 DEG C, and the treatment time is 6h, and the temperature of secondary solution treatment is 530 DEG C, and the treatment time is 2h;
(2), to the Al-Si-Cu-Mg casting alloy cooling 10s after double_stage guide process, cooling temperature is 18 DEG C;
(3) two-stage time effect process is adopted to cooled Al-Si-Cu-Mg casting alloy, complete the thermal treatment of Al-Si-Cu-Mg casting alloy.Wherein, the temperature of one-level ageing treatment is 180 DEG C, and the treatment time is 6h, for the temperature and time of second-stage treatment, adopts eight embodiments to be described this case below respectively, chooses best treatment temp by contrast and analysis.
Embodiment 1
The temperature of secondary time effect process is 200 DEG C, and the treatment time is 1h.
Embodiment 2
The temperature of secondary time effect process is 200 DEG C, and the treatment time is 2h.
Embodiment 3
The temperature of secondary time effect process is 200 DEG C, and the treatment time is 5h.
Embodiment 4
The temperature of secondary time effect process is 200 DEG C, and the treatment time is 10h.
In embodiment 1 ~ 4, the temperature of secondary time effect process is higher than the temperature of one-level ageing treatment, and four embodiments are labeled as H1 ~ H4 respectively successively, and the tensile strength (Stress) in treating processes and unit elongation (Strain) index are shown in Fig. 1.
Embodiment 5
The temperature of secondary time effect process is 100 DEG C, and the treatment time is 0.5h.
Embodiment 6
The temperature of secondary time effect process is 100 DEG C, and the treatment time is 1h.
Embodiment 7
The temperature of secondary time effect process is 100 DEG C, and the treatment time is 5h.
Embodiment 8
The temperature of secondary time effect process is 100 DEG C, and the treatment time is 10h.
In embodiment 5 ~ 8, the temperature of secondary time effect process is lower than the temperature of one-level ageing treatment, in embodiment 1 ~ 4, the temperature of secondary time effect process is higher than the temperature of one-level ageing treatment, four embodiments are labeled as L1 ~ L4 respectively successively, and the tensile strength (Stress) in treating processes and unit elongation (Strain) index are shown in Fig. 1.
Al-Si-Cu-Mg casting alloy performance index after process see the following form:
For the Al-Si-Cu-Mg casting alloy index selected by engine cylinder-body, cylinder cap, choose the treatment process that embodiment 3 adopts, for the Al-Si-Cu-Mg casting alloy of preferred proportion, this case additionally uses a comparison example, adopt T6 technique to process this Al-Si-Cu-Mg casting alloy, its contrasting data is as follows:
Interpretation of result:
The research of forefathers mainly concentrates on the order change of solid solution process interalloy microtexture and the impact on mechanical property.Solution treatment comprises the selection of solid solubility temperature and solution time.Suitable solid solubility temperature and time can ensure that the precipitated phase of alloy is all dissolved in matrix, can not cause crystal boundary burning again.Ageing treatment is carried out after solution treatment and quenching, and this just controls feature and the mechanical property of alloy phase precipitation.
This traditional single step aging strengthening model of T6 can not obtain best mechanical property.By age hardening process, mechanical property is strengthened, this is main relevant with the interaction of dislocation and precipitated phase.And in ag(e)ing process, the precipitated phase of Al-Si-Cu-Mg alloy can comprise Cu and Mg element simultaneously, and this phase has confirmed it is Q phase (Al in an experiment
5mg
8si
6cu
2).These precipitated phases, β-Mg
2si phase or Q phase all have close contacting with aging temp and time.When timeliness temperature and time raises, in some Al-Si-Cu-Mg alloys, the shared volume fraction of Q phase can increase.Simultaneously, relevant research finds, along with aging temp and the reduction of time, can form a large amount of CP-I districts and nascent β precipitated phase in Al-Si-Cu-Mg alloy, but under low-temperature condition, the Time-activity-curve of Al-Si-Cu-Mg alloy is recorded less in existing documents and materials.Therefore, in order to the precipitated phase of control Al-Si-Cu-Mg alloy, obtain best mechanical property, select multistage aging process to be necessary.
Mechanics property analysis test result shows: the strength of alloy under this case process ration T6 technique improves 9.5%, and unit elongation, namely plasticity decline and not obvious, only have dropped 0.02%.Under the prerequisite ensureing plasticity, significantly improve the intensity of alloy, take into account the balance of strength of alloy in alloy production and unit elongation thus, overcome the technical barrier of certain art technology, this heat treated mode is not only embodied in theory, but can be widely used in the heat treated industrial production of Al-Si-Cu-Mg casting alloy.
Al-Si-Cu-Mg casting alloy provided by the invention, extends the scope of application in Alloyapplication field, and especially for the alloy material of automobile engine cylinder-body and cylinder cap, its intensity and plasticity meet the requirements just; On the other hand, production castmethod provided by the invention achieves the object of loss of weight, reaches the light-weight design requirement of product, thus realizes the target of energy-saving and emission-reduction.
Although disclose embodiments of the invention and accompanying drawing for the purpose of illustration, but it will be appreciated by those skilled in the art that: in the spirit and scope not departing from the present invention and claims, various replacement, change and amendment are all possible, therefore, scope of the present invention is not limited to the content disclosed in embodiment and accompanying drawing.
Claims (6)
1. an Al-Si-Cu-Mg casting alloy, this casting alloy electrolytic aluminum, Pure Silicon Metal, pure magnesium and the melting of Al-Cu master alloy form, it is characterized in that: its feed composition and weight percent thereof are respectively: Si:5.5 ~ 6.5%, Cu:1.8 ~ 2.2%, Mg:0.45 ~ 0.55%, Fe: be less than 0.15%, Ti:0.10 ~ 0.15%, Mn: be less than 0.05%, Zn: be less than 0.05%, other impurity are less than 0.01%, all the other are Al, and wherein Cu/Mg is than being 4:1.
2. Al-Si-Cu-Mg casting alloy according to claim 1, it is characterized in that: feed composition and the weight percent thereof of described Al-Si-Cu-Mg casting alloy are respectively: Si:5.98%, Cu:2.08%, Mg:0.52%, Fe:0.02%, Ti: be less than 0.01%, Mn: be less than 0.01%, Zn: be less than 0.01%, other impurity are less than 0.01%, and all the other are Al.
3. a heat treating method for Al-Si-Cu-Mg casting alloy as claimed in claim 1 or 2, is characterized in that: the steps include:
(1) double_stage guide process is adopted to described Al-Si-Cu-Mg casting alloy;
(2) to the Al-Si-Cu-Mg casting alloy cooling after double_stage guide process;
(3) two-stage time effect process is adopted to cooled Al-Si-Cu-Mg casting alloy, wherein the temperature of one-level ageing treatment is 180 DEG C, and the treatment time is 6h, and the temperature of secondary time effect process is 100 ~ 200 DEG C, treatment time is 0.5 ~ 2h, completes the thermal treatment of Al-Si-Cu-Mg casting alloy.
4. the heat treating method of Al-Si-Cu-Mg casting alloy according to claim 3, it is characterized in that: in the double_stage guide process that step is (1) described, the temperature of one-level solution treatment is 470 DEG C, and the treatment time is 6h, the temperature of secondary solution treatment is 530 DEG C, and the treatment time is 2h.
5. the heat treating method of Al-Si-Cu-Mg casting alloy according to claim 3, is characterized in that: the (2) described cooling temperature of step is 18 DEG C, and cooling time is 10s.
6. the heat treating method of Al-Si-Cu-Mg casting alloy according to claim 3, is characterized in that: the temperature of the secondary time effect process of the two-stage time effect process that step is (3) described is 200 DEG C, and the treatment time is 5h.
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| CN109468499A (en) * | 2018-11-26 | 2019-03-15 | 齐鲁工业大学 | A kind of the Al-Si-Cu-Mg-Zn cast alloy materials and its aging technique of high-strength and high ductility |
| CN110951982A (en) * | 2019-11-29 | 2020-04-03 | 辽宁忠旺集团有限公司 | Production process for improving intergranular corrosion resistance of 6-series aluminum alloy |
| CN111363990A (en) * | 2020-03-25 | 2020-07-03 | 广东省工业分析检测中心 | Heat treatment method of lead-free-cutting aluminum alloy extruded bar |
| CN112322947A (en) * | 2020-11-11 | 2021-02-05 | 西北工业大学 | High-strength plastic Al-Mg-Si-Zn alloy for automobile and preparation method thereof |
| CN113584334A (en) * | 2021-08-12 | 2021-11-02 | 江苏库纳实业有限公司 | Production process of aluminum alloy section for automobile |
| CN113584412A (en) * | 2021-06-01 | 2021-11-02 | 青岛科麟航空科技有限公司 | Heat treatment method of ZL105A casting and ZL105A casting |
| CN114250388A (en) * | 2021-12-29 | 2022-03-29 | 北京理工大学 | High-strength cast aluminum-silicon alloy part with complex shape for automobile and preparation method thereof |
| CN115418513A (en) * | 2022-09-23 | 2022-12-02 | 北京航空航天大学云南创新研究院 | High-strength heat-resistant cast aluminum-silicon alloy and heat treatment method thereof |
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| CN109468499A (en) * | 2018-11-26 | 2019-03-15 | 齐鲁工业大学 | A kind of the Al-Si-Cu-Mg-Zn cast alloy materials and its aging technique of high-strength and high ductility |
| CN110951982A (en) * | 2019-11-29 | 2020-04-03 | 辽宁忠旺集团有限公司 | Production process for improving intergranular corrosion resistance of 6-series aluminum alloy |
| CN111363990A (en) * | 2020-03-25 | 2020-07-03 | 广东省工业分析检测中心 | Heat treatment method of lead-free-cutting aluminum alloy extruded bar |
| CN112322947A (en) * | 2020-11-11 | 2021-02-05 | 西北工业大学 | High-strength plastic Al-Mg-Si-Zn alloy for automobile and preparation method thereof |
| CN113584412A (en) * | 2021-06-01 | 2021-11-02 | 青岛科麟航空科技有限公司 | Heat treatment method of ZL105A casting and ZL105A casting |
| CN113584334A (en) * | 2021-08-12 | 2021-11-02 | 江苏库纳实业有限公司 | Production process of aluminum alloy section for automobile |
| CN114250388A (en) * | 2021-12-29 | 2022-03-29 | 北京理工大学 | High-strength cast aluminum-silicon alloy part with complex shape for automobile and preparation method thereof |
| CN115418513A (en) * | 2022-09-23 | 2022-12-02 | 北京航空航天大学云南创新研究院 | High-strength heat-resistant cast aluminum-silicon alloy and heat treatment method thereof |
| CN115418513B (en) * | 2022-09-23 | 2023-09-29 | 北京航空航天大学云南创新研究院 | High-strength heat-resistant cast aluminum-silicon alloy and heat treatment method thereof |
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