CN101775529A - High-strength cast aluminum-silicon alloy for engine body and preparation method thereof - Google Patents
High-strength cast aluminum-silicon alloy for engine body and preparation method thereof Download PDFInfo
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Abstract
The invention relates to a high-strength cast aluminum-silicon alloy for an engine body and a preparation method thereof, belonging to the field of metal materials. The alloy comprises the following components in percentage by weight: 12.0-14.0% of Si, less than 0.3% of Ni, 3.0-5.0% of Cu, 0.3-0.8% of Fe, 0.4-0.8% of Mn, less than 0.4% of Mg, 0.1-0.2% of Ti, less than 0.27wt% of Zr and balance of Al. Heat treatment parameters are as follows: the solution treatment is carried out at 510+/-5 DEG C for 5-8h and then water quenching is carried out at room temperature; and the aging treatment is carried out at 160+/-5 DEG C for 6-10h and then air cooling is carried out. The tensile strength and the yield strength of the alloy at room temperature after heat treatment respectively reach 316-336MPa and 245-263MPa, the elongation of the broken alloy reaches 0.72-0.83%, and the Brinell hardness reaches 155-166HBW to the maximum. Compared with the similar alloys, the alloy of the invention has the advantages of high mechanical properties, low content of Ni elements, reduction of content of noble elements in the alloy, wider allowed fluctuation range of content of Fe elements, good cast ingot quality, simple processes and strong operability.
Description
Technical field
The invention belongs to metal material field, relate to a kind of high-strength cast aluminum-silicon alloy for engine body and preparation method thereof, particularly this alloy pairing melting and thermal treatment process in its composition range.
Background technology
Complicated mechanical load such as during engine operation, body continues to bear tensile, compressive, bending, turn round; High-temperature fuel gas directly contacts in cylinder wall and the combustion chamber, bears higher thermal load for a long time.In order to satisfy the requirement of bad working environment to material, the used alloy of preparation body should have enough strength and stiffness, and has good wear-resisting and corrosion resistance.
Alleviating car weight, raising speed under the energy-conservation industry background, the application of cast aluminium alloy body on engine is more and more general.Engine body cast aluminium alloy commonly used has AA319, AA356, AC4B, ZL101, the trades mark such as ZL107.The characteristics of this class alloy are to have the medium tenacity performance, and manufacturing cost is lower, are fit to commercially produce, but when preparing cylinder body with this class alloy, all need with cylinder sleeve or carry out surface treatment and satisfy abrasion resistance properties required in the body work.Lining is placed in the mold or inserts in the mach cylinder thorax, and this processing mode of cylinder body will certainly increase the cost of product.In order to address this problem, just to need a kind of novel casting aluminum alloy that not only had been fit to the cylinder body manufacturing but also had had an excellent abrasive resistance to be used as substituting and use material.
The common method that improves this class cast Al-Si alloy performance is that the composition and the production technique of material are adjusted.Have specifically following some:
1) improve the content of Ni element in the matrix, add a certain amount of V simultaneously, Sc, Cr, Mo, noble elements such as Ta, and in the control alloy Fe content within the specific limits, representative patents has: US5996471A, US4681736, US4975243;
2) improve preparation technology, control melt solidifying process makes solid state growth speed (R) and liquid-solid interface thermograde (G) than in proper range, and representative patents has: US4434014, US5019178;
3) obtain the ideal structure property in conjunction with certain hot-work and thermal treatment process, representational patent has CN100439533C, US4934442.
As seen, in the above measure that improves this class alloy property, or increase the content of noble element in the composition, or adopt special preparation and complete processing.Though this is improved alloy property to a certain extent, also caused the significantly increase of production cost.This situation has hindered popularization and the application of this class alloy under the general industry working condition.
Summary of the invention
The objective of the invention is to solve engine body and cause expensive contradiction with the high-performance that cast Al-Si alloy exists.Under the prerequisite that does not increase production cost, increase substantially the mechanical property of alloy, with the development of satisfying automobile industry requirement to alloy mechanics mechanical property.
A kind of high-strength cast aluminum-silicon alloy for engine body and preparation method thereof.The composition range of alloy is:
Si:12.0-14.0wt%; Ni:＜0.3wt%; Cu:3.0-5.0wt%; Fe:0.3-0.8wt%; Mn:0.4-0.8wt%; Mg:＜0.4wt%; Ti:0.1-0.2wt%; All the other are Al for Zr:＜0.27wt%..
Purity＞the 99.0wt% of Al element wherein, other elements all add with the form of master alloy, and used master alloy is as follows:
Al-37.0wt％Si；Al-10.0wt％Ni；Al-45.0wt％Cu；Al-6.0wt％Fe；Al-10.0wt％Mn；Al-10.0wt％Mg；Al-5.0wt％Ti；Al-4.0wt％Zr。
The preparation process of mentioned component cast Al-Si alloy is as follows:
1) preparation of melting apparatus and raw material and oven dry (bake out temperature is controlled at 200 ℃);
2) put into raw material by different level, low melting point low density raw material is placed on bottom, and high-melting-point high-density raw material is placed on the upper strata, it is as follows to lay order: Al-10.0wt%Mg, Al-37.0wt%Si, Al-10.0wt%Mn, Al-6.0wt%Fe, Al-10.0wt%Ni, Al-45.0wt%Cu;
3) smelting temperature is 800 ℃, when treating that alloy in the pasty state with bell jar with Al-5.0wt%Ti; Al-4.0wt%Zr is pressed into crucible bottom together, spreading flux on melt;
4) treat that alloy melts fully after, stir slagging-off and be pressed into the AlP alterant, at 800 ℃ of insulation 30-40min;
5) cool to 750-760 ℃, deslagging refining, with dry Ar gas (or hexachloroethane) refining 1-2 minute, the nozzle of logical Ar gas was pressed into about 1/3 place of crucible bottom;
6) leave standstill 10-15min, when dropping to 710-720 ℃ etc. furnace temperature the melt quick and stable pour in the metal die that is preheating to 175-185 ℃.
Aforesaid operations is done some explanation:
Used flux is the 50wt%NaCl+50wt%KCl powder, and granularity≤125 μ m are advisable, and add-on is controlled at the 3-5wt% of melt total amount;
Al-Ti, it is in order to reduce Ti, the scaling loss of Zr element, the effective content of raising element in melt that the Al-Zr hysteresis adds;
Deterroration and soaking time are to determine that the add-on of P is controlled at the 0.08-0.1wt% of melt total mass in the AlP alterant incubation period in melt by the AlP alterant;
Low temperature waters the castability that can improve this alloy soon.
After cast finishes, the gained foundry goods is heat-treated, processing parameter is:
Solution treatment: 510 ± 5 ℃ * 5-8h+ room temperature shrend;
Ageing treatment: 160 ± 5 ℃ * 6-10h+ air cooling.
The present invention develops preparation and the thermal treatment process of a kind of novel high-strength engine body with cast Al-Si alloy and this alloy.Adopt the casting of plain metal mould, by composition and the technology of optimizing this alloy, make its room temperature tensile strength and yield strength reach 316-336MPa and 245-263MPa respectively, elongation after fracture reaches 0.72-0.83%, and Brinell hardness is up to 155-166HBW.Compared with prior art, its advantage is:
1) with alloy phase ratio of the same type, reduced the content of Ni element, reduced the content of noble element in the alloy;
2) the present invention has optimized Cu in the alloy, and the Fe constituent content under plain metal die cast technology, is brought up to 0.8wt% to Fe content alloy strength is remained on more than the 335MP;
3) the present invention has added micro-Zr element in alloying constituent, plays crystal grain thinning, strengthens matrix, the effect that further improves structure stability;
4) do not need on the preparation technology to carry out other special operationals, ingot quality is good, and technology is simple, and is workable.
Description of drawings
Fig. 1 is the metallographic structure photo of application example alloy CF3 of the present invention
Fig. 2 is the metallographic structure photo of application example alloy CF8 of the present invention
Fig. 3 is the fracture SEM photo of application example alloy CF3 of the present invention
Fig. 4 is the fracture SEM photo of application example alloy CF8 of the present invention
Fig. 5 is the back scattering photo of application example alloy CF3 of the present invention
Fig. 6 is the back scattering photo of application example alloy CF8 of the present invention
Fig. 1 and Fig. 2 are metallographic structure photos after the alloy heat treatment, can find out the sharp corners of having eliminated primary silicon after P goes bad, and particle obtains refinement, and average-size is below 15 μ m; Eutectic Silicon in Al-Si Cast Alloys after heat treatment fuses and is tiny graininess, is distributed in the matrix to disperse. Just/Eutectic Silicon in Al-Si Cast Alloys distribution of small and dispersed in matrix is to improve one of principal element of this alloy mechanical property.
Fig. 3 and Fig. 4 are alloy stretching sample fracture SEM photos, can find out, fracture has dimple fracture and the standard fracture shape characteristic that dissociates simultaneously. Along with the increase of tensile load, dislocation be mingled with, just/constantly concentrate around Eutectic Silicon in Al-Si Cast Alloys and the intermetallic compound particle; Dislocation can't be cut casting flaw and precipitated phase, can only move with bypass mechanism, thus long-pending at a large amount of plugs of boundary, cause interfacial stress to be concentrated, boundary is separated, hard and crisp second-phase is cracked under effect of stress, cracks the source.
Dimple columnar fracture focuses mostly on around the tiny Al2Cu particle of separating out in the matrix after heat treatment. This is that the elements such as Si dissolve in the supersaturated solid solution of Al matrix forming component complexity because alloy solid solution is processed rear Cu and a small amount of Mg, makes matrix strength improve toughness drop; In ag(e)ing process subsequently, the Cu element is separated out with the form of Al2Cu, cause the significantly minimizing of solid solution Cu element near the matrix of precipitated phase, matrix toughness improves on the contrary, therefore topical manifestations goes out the ductile fracture feature in deformation process, form dimple columnar fracture, this process belongs to the ductile fracture of high energy absorption process.
Fractograph shows the fracture of dissociating that is as the criterion mostly, and tearing the mountain range is a kind of the most basic fracture apperance feature of quasi-cleavage crack. It is generally acknowledged that the microscopic appearance feature of quasi-cleavage crack has reflected cleavage crack and the relation that the intergranular interaction of plastic deformation takes place to a certain extent.
Figure 4 shows that the rich Fe phase dendrite that exists in the example alloy, a dendrite size is about 15 μ m. Have the not yet fully secondary dendrite of growth at a dendrite, this is relevant with the melt cooling speed. There is obvious I type crackle in the dendrite, can judges that from its tendency this crackle is to produce under the effect of stress that the dendrite tip height is concentrated. According to the theory of Griffith, the reduction of the elastic strain energy of storage is more than or equal to forming two required surface energies in new surface owing to ftracture in the object, and the reduction of the elastic strain energy of namely storing in the object (or release) is the power of Crack Extension. So the existence of this type of rich Fe phase to a certain extent relieve stresses is concentrated, and absorbs strain energy, stop crackle to further expand.
Fig. 5 and Fig. 6 are the back scattering photos of organizing after the alloy heat treatment, can find out that intermetallic compound separates out pattern in alloy substrate. Energy spectrum analysis finds, precipitated phase take rich Cu phase and rich Fe mutually as main. The rich Cu of a part forms in melt in the process of setting, is block distribution around rich Fe phase; Another part is to separate out in matrix after the heat treatment, and this class is separated out to tiny white granular and is distributed in the matrix. Rich Fe exists with herring-bone form cluster form, and along with the increase of Fe content, rich Fe intermetallic compound cluster quantity increase, the Fe element can improve matrix yield strength at high temperature. Between this two metalloid compound separate out the generation dispersion-strengthened effect, put forward heavy alloyed mechanical property.
Table 1 and table 2 column data is to the present invention relates to alloy and several trade mark Birmasil room temperature tensile performance commonly used and Brinell hardness contrast, and as seen, the example alloy mechanical property surpasses Japan
Table 1. example alloy and several trade mark Birmasil room temperature tensile performance data commonly used
Annotate: 1) ADC10, ADC12, the corresponding performance of AC4B is die casting T6 condition of heat treatment;
2) GZL-1 is a kind of high strength low pressure casting alusil alloy that China CN1483848A patent is announced.
Table 2 example alloy and several trade mark Birmasil Brinell hardness data commonly used
The heat treated ADC12 trade mark of die casting alloy. Brinell hardness surpasses the hypereutectic A390 alloy of die cast. Alloy rigidity is more high, and wearability is more good, and the example alloy not only has good strength character, also has higher hardness and wearability.
In general, the impurity element that Fe is considered in the Production of casting Al alloys is rejected, and its too high levels is difficult to reach corresponding trade mark regulation mechanical property with general casting method; Ni is considered to improve the beneficial element of alloy structure performance, usually this constituent content is remained on more than the 0.8wt% in the production; And the example alloy can obtain desirable combination property adopt common metal die cast and heat treatment in the composition range of the low high Fe of Ni after, is a kind of novel casting aluminum alloy with good practicality.
Embodiment
Embodiment 1: alloy smelting is grouped into by following one-tenth:
Si:12.5wt%; Ni:0.25wt%; Cu:5.0wt%; Fe:0.3wt%; Mn:0.5wt%; Mg:0.3wt%; Ti:0.15wt%; Zr:0.27wt%. all the other are Al.
Example alloy numbering: CF3.
The alloy preparation process is as follows: at crucible bottom spreading one deck flux, (purity＞99.0wt%) and master alloy are put into crucible by different level, and the fusing point low density is little is placed on lower floor, and the fusing point high-density is big is placed on the upper strata with commercial-purity aluminium then; Furnace temperature is risen to 780 ℃, when insulation treats that raw material in the pasty state with bell jar with Al-Ti, the Al-Zr master alloy is pressed into crucible bottom, subsequently at bath surface spreading flux; After raw material melts fully, insert melt with clean Ti rod and stir the 3-5 circle gently, remove the bath surface slag; At twice AlP is pressed into the melt processing of going bad with bell jar, treats that it melts the back fully and takes out bell jar, is warming up to 800 ℃, insulation 30min; Then furnace temperature is dropped to 750-760 ℃, after the slagging-off dry Ar gas is fed the about 1/3 place refining of crucible bottom 1-2 minute; Leave standstill 15-20min, blow-on slagging-off when dropping to 710-720 ℃ etc. furnace temperature, with the melt quick and stable pour in the metal die that is preheating to 175-185 ℃.
Ingot casting is implemented following thermal treatment process:
Solution treatment: 510 ± 5 ℃ * 5-8h+ room temperature shrend;
Ageing treatment: 160 ± 5 ℃ * 6-10h+ air cooling.
The mechanical property of alloy: tensile strength 316MPa after the thermal treatment; Yield strength: 245MPa; Unit elongation: 0.83%, maximum Brinell hardness: 155HBW.
Embodiment 2: alloy smelting is grouped into by following one-tenth:
Si:13.5wt%; Ni:0.3wt%; Cu:5.0wt%; Fe:0.8wt%; Mn:0.6wt%; Mg:0.4wt%; Ti:0.10wt%; Zr:0.27wt%. all the other are Al.
Example alloy numbering: CF8.
The alloy preparation process is as follows: at crucible bottom spreading one deck flux, (purity＞99.0wt%) and master alloy are put into crucible by different level, and the fusing point low density is little is placed on lower floor, and the fusing point high-density is big is placed on the upper strata with commercial-purity aluminium then; Furnace temperature is risen to 780 ℃, when insulation treats that raw material in the pasty state with bell jar with Al-Ti, the Al-Zr master alloy is pressed into crucible bottom, subsequently at bath surface spreading flux; After raw material melts fully, insert melt with clean Ti rod and stir the 3-5 circle gently, remove the bath surface slag; At twice AlP is pressed into the melt processing of going bad with bell jar, treats that it melts the back fully and takes out bell jar, is warming up to 800 ℃, insulation 30min; Then furnace temperature is dropped to 750-760 ℃, after the slagging-off dry Ar gas is fed the about 1/3 place refining of crucible bottom 1-2 minute; Leave standstill 15-20min, blow-on slagging-off when dropping to 710-720 ℃ etc. furnace temperature, with the melt quick and stable pour in the metal die that is preheating to 175-185 ℃.
Ingot casting is implemented following thermal treatment process:
Solution treatment: 510 ± 5 ℃ * 5-8h+ room temperature shrend;
Ageing treatment: 160 ± 5 ℃ * 6-10h+ air cooling.
The mechanical property of alloy: tensile strength 336MPa after the thermal treatment; Yield strength: 263MPa; Unit elongation: 0.72%, maximum Brinell hardness: 161HWB.
Claims (2)
1. high-strength cast aluminum-silicon alloy for engine body is characterized in that basic composition is:
Si:12.0-14.0wt%; Ni:＜0.3wt%; Cu:3.0-5.0wt%; Fe:0.3-0.8wt%; Mn:0.4-0.8wt%; Mg:＜0.4wt%; Ti:0.1-0.2wt%; Zr:＜0.27wt%, all the other are Al.
2. the preparation method of a kind of high-strength cast aluminum-silicon alloy for engine body as claimed in claim 1 is characterized in that preparing purity＞99.0wt% of the used metal element A l of alloy, and other elements all close with the centre
The form of gold adds, and used master alloy composition proportion is as follows: Al-37.0wt%Si; Al-10.0wt%Ni; Al-45.0wt%Cu; Al-6.0wt%Fe; Al-10.0wt%Mn; Al-10.0wt%Mg; Al-5.0wt%Ti; Al-4.0wt%Zr, preparation process is as follows:
1) preparation of melting apparatus and raw material and oven dry, bake out temperature are controlled at 200 ℃;
2) put into raw material by different level, low melting point low density raw material is placed on bottom, and high-melting-point high-density raw material is placed on the upper strata, concrete order is as follows: Al-10.0wt%Mg, Al-37.0wt%Si, Al-10.0wt%Mn, Al-6.0wt%Fe, Al-10.0wt%Ni, Al-45.0wt%Cu;
3) smelting temperature is 800 ℃, Al-5.0wt%Ti and Al-4.0wt%Zr is pressed into crucible bottom together, spreading flux with bell jar when treating that added alloy in the pasty state;
4) treat that all alloys melt fully after, stir to remove slag and be pressed into the AlP alterant, at 800 ℃ of insulation 30-40min;
5) cool to 750-760 ℃, deslagging refining, with dry Ar gas or hexachloroethane refining 1-2 minute, the nozzle of logical Ar gas was pressed into about 1/3 place of crucible bottom;
6) leave standstill 10-15min, when dropping to 710-720 ℃ etc. furnace temperature the melt quick and stable pour in the metal die that is preheating to 175-185 ℃;
7) after cast finishes, the gained foundry goods is heat-treated, processing parameter is:
Solution treatment: 510 ± 5 ℃ * 5-8h+ room temperature shrend;
Ageing treatment: 160 ± 5 ℃ * 6-10h+ air cooling.
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| CN102676961A (en) * | 2012-05-17 | 2012-09-19 | 中北大学 | Heat treatment method of copper-rich cast hypoeutectic aluminum-silicon alloy |
| CN103736977A (en) * | 2013-12-30 | 2014-04-23 | 金陵科技学院 | Method for casting aluminum alloy |
| CN104372188A (en) * | 2013-08-16 | 2015-02-25 | 中国科学院金属研究所 | Preparation method of high silicon nickel-copper alloy casting |
| CN105779743A (en) * | 2016-05-06 | 2016-07-20 | 扬州大学 | Aging treatment method for accurate die-cast cylinder body of auto air-condition compressor |
| CN107419117A (en) * | 2017-07-27 | 2017-12-01 | 广州致远新材料科技有限公司 | The preparation method and wear-resistant aluminum alloy of a kind of wear-resistant aluminum alloy |
| CN107447137A (en) * | 2017-07-31 | 2017-12-08 | 江苏大学 | The high tough corrosion-resistant Al Si Cu cast aluminium alloy golds and preparation method of a kind of Zr and Sr combined microalloyings |
| CN108823438A (en) * | 2018-07-03 | 2018-11-16 | 云南云铝涌鑫铝业有限公司 | The method for preparing the low ferroaluminium of ZLD102 |
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| CN111640474A (en) * | 2020-05-15 | 2020-09-08 | 合肥通用机械研究院有限公司 | Centrifugal casting alloy material design method with preset microstructure |
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| CN102676961A (en) * | 2012-05-17 | 2012-09-19 | 中北大学 | Heat treatment method of copper-rich cast hypoeutectic aluminum-silicon alloy |
| CN104372188A (en) * | 2013-08-16 | 2015-02-25 | 中国科学院金属研究所 | Preparation method of high silicon nickel-copper alloy casting |
| CN104372188B (en) * | 2013-08-16 | 2016-08-24 | 中国科学院金属研究所 | A kind of preparation method of high tantnickel copper-alloy casting |
| CN103736977A (en) * | 2013-12-30 | 2014-04-23 | 金陵科技学院 | Method for casting aluminum alloy |
| CN103736977B (en) * | 2013-12-30 | 2016-01-27 | 金陵科技学院 | A kind of method of Birmasil |
| CN105779743A (en) * | 2016-05-06 | 2016-07-20 | 扬州大学 | Aging treatment method for accurate die-cast cylinder body of auto air-condition compressor |
| CN107419117A (en) * | 2017-07-27 | 2017-12-01 | 广州致远新材料科技有限公司 | The preparation method and wear-resistant aluminum alloy of a kind of wear-resistant aluminum alloy |
| CN107447137A (en) * | 2017-07-31 | 2017-12-08 | 江苏大学 | The high tough corrosion-resistant Al Si Cu cast aluminium alloy golds and preparation method of a kind of Zr and Sr combined microalloyings |
| CN108823438A (en) * | 2018-07-03 | 2018-11-16 | 云南云铝涌鑫铝业有限公司 | The method for preparing the low ferroaluminium of ZLD102 |
| CN109402473A (en) * | 2018-12-11 | 2019-03-01 | 贵州大学 | A kind of Al-Si-Cu-Mn heat-resisting aluminium alloy and preparation method thereof with high Fe content |
| CN109609822A (en) * | 2019-02-14 | 2019-04-12 | 贵州大学 | A kind of semi-solid forming aluminium alloy and preparation method thereof |
| CN111945038A (en) * | 2019-05-16 | 2020-11-17 | 马勒国际有限公司 | Method for producing an engine component, engine component and use of an aluminium alloy |
| CN111640474A (en) * | 2020-05-15 | 2020-09-08 | 合肥通用机械研究院有限公司 | Centrifugal casting alloy material design method with preset microstructure |
| CN111640474B (en) * | 2020-05-15 | 2022-09-23 | 合肥通用机械研究院有限公司 | Centrifugal casting alloy material design method with preset microstructure |
| WO2023015578A1 (en) * | 2021-08-11 | 2023-02-16 | 江苏大学 | Al-si-cu-fe-mn alloy and preparation method therefor |
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Open date: 20100714 |