CN104313413B - A kind of Al-Mg-Zn system alloy and the preparation method of sheet alloy thereof - Google Patents

A kind of Al-Mg-Zn system alloy and the preparation method of sheet alloy thereof Download PDF

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CN104313413B
CN104313413B CN201410577461.5A CN201410577461A CN104313413B CN 104313413 B CN104313413 B CN 104313413B CN 201410577461 A CN201410577461 A CN 201410577461A CN 104313413 B CN104313413 B CN 104313413B
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alloy
sample
sheet
follows
plate materials
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CN201410577461.5A
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CN104313413A (en
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张迪
候胜利
张济山
庄林忠
刘君城
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北京科技大学
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    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C21/00Alloys based on aluminium
    • C22C21/06Alloys based on aluminium with magnesium as the next major constituent
    • C22C21/08Alloys based on aluminium with magnesium as the next major constituent with silicon
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C21/00Alloys based on aluminium
    • C22C21/06Alloys based on aluminium with magnesium as the next major constituent
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22FCHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/047Changing 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 magnesium as the next major constituent

Abstract

A kind of Al Mg Zn system's alloy and the preparation method of sheet alloy thereof, belong to non-ferrous metal field.The mass percentage content of Al Mg Zn system alloy is, 4.0~5.7%Mg, 2.5~4.0%Zn, 0~0.4%Cu, 0.4~1.2%Mn, 0~0.1%Cr, 0~0.15%Ti, 0.05~0.25%Zr, 0~0.4%Fe, 0~0.4%Si, and remaining is Al.This alloy makes full use of the main hardening constituent η MgZn of Al Zn Mg Cu series alloy2And T Mg2Al3Zn3And the invigoration effect of transitional face, use the preparation technology of the present invention, make this alloy have the ageing strengthening effect of excellence during Precipitation.Relative to traditional H131 cold rolling state sheet material, be there is more excellent intensity and elongation percentage by the alloy T6 state sheet material prepared by the present invention.Prepared sheet alloy is applicable to the aluminium alloy association area such as plate armour and boats and ships.

Description

A kind of Al-Mg-Zn system alloy and the preparation method of sheet alloy thereof
Technical field
The invention belongs to non-ferrous metal and preparation field thereof, particularly relate to a kind of high intensity can the Al-Mg-Zn type alloy of industrial applications, and the plate product prepared by this alloy.
Background technology
In order to reduce fuel used to generate power and improve the benefit of maximum dimensions of vehicle, reducing construction weight has been a kind of inevitable trend.The 5 ××× line aluminium alloys of high Mg have good corrosion resistance, formability, solderability and moderate strength, it it is armoring and one of the optimal selection of boats and ships loss of weight sheet material, if 5 ××× line aluminium alloys of H321 and H116 state are the important feature materials of large ship sheet material, 5 ××× line aluminium alloys of H131 and H136 state are then widely used in military armor car outside plate and tank base plate.The alloys such as current the most existing AA5083, AA5383 and AA5059 all achieve the application of successful in this field.The AA5059 alloy that wherein association of Alcoa registers for 1999 is greatly improved the content of Mg, Zn and Cu in alloy on the basis of AA5083 alloy, on the premise of keeping elongation percentage to be basically unchanged, significantly improve yield strength and the tensile strength of alloy, keep the corrosion resistance of alloy to be not less than AA5083 alloy simultaneously.This alloy the most progressively occupies plate armour and the market in Marine Materials field with the combination property of its excellence.
It is 4.0 to 4.9 that the compositing range of above-mentioned three kinds of alloys is respectively as follows: AA5083:Mg content, and Mn content is 0.4 to 1.0, and Cr content is 0.05 to 0.25, Zn content is up to 0.25, and Cu content is up to 0.1, and Ti content is up to 0.15, Fe content is up to 0.4, and Si content is up to 0.4;AA5383:Mg content is 4.0 to 5.2, and Mn content is 0.7 to 1.0, and Cr content is up to 0.25, and Zn content is up to 0.4, and Cu content is up to 0.2, and Ti content is up to 0.15, and Fe content is up to 0.25, and Si content is up to 0.25, and Zr content is up to 0.2;AA5059:Mg content is 5.0 to 6.0, and Mn content is 0.6 to 1.2, and Cr content is up to 0.25, Zn content is 0.4 to 0.9, and Cu content is up to 0.25, and Ti content is up to 0.2, Fe content is up to 0.5, and Si content is up to 0.45, and Zr content is 0.05 to 0.25.During wherein AA5059 alloy is also disclosed in US-6695935-B1, US-6238495-B1, CN-101233252-A and CN-101631882-A patent.
The patent (application number 201410117124.8) that we have applied for is on the basis of AA5059 alloy, the content of Zn during trace improves alloy further, by the processing technology of optimized alloy, further increase the mechanical property of alloy H131 state and the mechanical property of H321 state and corrosion resistance.This alloy can be applied not only to Marine Materials field, also can be used as armour plate material etc. simultaneously.Another part of patent (application number 201410381094.1) continues to add Zn content and by the processing technology of optimized alloy on this basis, increases the cold rolling amount of alloy, significantly improves intensity and the anti intercrystalline corrosion performance of alloy.
The present invention forms spherical GP district → η ' → η (MgZn based on Al-Zn-Mg (7xxx system) alloy precipitation precipitation2), spherical GP district → T' → T (Al2Mg3Zn3), fixation rates plays the scientific thought of precipitation strength effect, it is proposed that the new ideas of 5xxx system alloy design.The relative solid solution content of Mg is reduced by introducing a large amount of Zn in 5xxx system alloy, a large amount of consumption Al-Mg precipitated phases, promote intracrystalline to generate a large amount of compound phase Han Zn, play precipitation strength effect.Adjust alloy solid solution composition, the 5xxx system alloy that can not be heat-treated precipitation strength is changed into can Precipitation enhanced type alloy, significantly improve the mechanical property of alloy.This is the essential distinction that this method and AA5059 alloy add a small amount of Zn.Thus the new alloy for research and development high-strength high-elongation ratio provides new approaches, has good research and application prospect.
Summary of the invention:
In order to overcome the deficiencies in the prior art, separate out dissatisfactory feature for conventional Al-Mg system alloy aging, develop a kind of new A l-Mg-Zn system alloy can strengthened with Precipitation, significantly improve the mechanical property of 5 ××× line aluminium alloys.
The present invention is designed by phasor composition and optimizes and first selects the composition range of Al-Mg-Zn alloy, then by the alloy designed by the processing technology preparations such as melting and casting, and its cold rolling state and Precipitation state are studied, finally determine that there is cold rolling state and the composition of Precipitation strengthening state Al-Mg-Zn alloy.
The first object of the present invention is to provide a kind of novel 5 ××× system Al-Mg-Zn alloys with high intensity, it is characterized in that the chemical composition of this alloy has mass percentage content and is: 4.0~5.7%Mg, 2.5~4.0%Zn, 0~0.4%Cu, 0.4~1.2%Mn, 0~0.1%Cr, 0~0.15%Ti, 0.05~0.25%Zr, 0~0.4%Fe, 0~0.4%Si, remaining is Al.
Preferably, the mass percentage content of described aluminium alloy is, 4.3~5.5%Mg, 2.5~3.5%Zn, 0~0.2%Cu, 0.6~1.0%Mn, 0~0.1%Cr, 0~0.15%Ti, 0.05~0.25%Zr, 0~0.2%Fe, 0~0.2%Si, and remaining is Al.
The second object of the present invention is to propose the preparation method of a kind of above-mentioned novel 5 ××× system Al-Mg-Zn alloys.Described alloy aging precipitation strength state sheet material preparation technology is as follows: the melting and casting of alloying component selection → alloy → two-step homogenization annealing → hot rolling deformation → intermediate annealing → cold roller and deformed → solid solution Water Quenching → twin-stage T6 Ageing Treatment.
Preferably, the two-step homogenization annealing process of described aluminum alloy plate materials is particularly as follows: start to be incubated 3~8h from room temperature to 425~440 DEG C with 20~40 DEG C/h heating rate by the alloy sample after melting and casting, it is continuously heating to 510~535 DEG C of insulations 5~15h with 20~40 DEG C/h heating rate the most again, is cooled to room temperature with 20~40 DEG C/h rate of temperature fall with stove the most again.
Preferably, the hot rolling deformation technique of described aluminum alloy plate materials, particularly as follows: sample is heated to 470~500 DEG C of insulation 2h, carries out the thermal deformation that deflection is more than 90%, and finishing temperature is more than 380 DEG C.
Preferably, the intermediate annealing process of described aluminum alloy plate materials particularly as follows: be heated to 350~450 DEG C of insulations 0.5~2h, then air cooling by sample.
Preferably, the cold roller and deformed technique of described aluminum alloy plate materials is particularly as follows: sample cold rolling reduction is 10~30%.
Preferably, solid solution and the Water Quenching technique of described aluminum alloy plate materials, particularly as follows: sample is incubated in the salt bath furnace of 500~535 DEG C 10~30min, the most directly carry out shrend.
Preferably, the twin-stage T6 aging treatment process of described aluminum alloy plate materials particularly as follows: sample to be carried out in the heat-treatment furnace of 50~100 DEG C the first order Ageing Treatment of 12~24h, the most again 110~160 DEG C carry out 10~30h second level Ageing Treatment.
Pass through technique scheme, the present invention has a following superiority: the novel 5 ××× system Al-Mg-Zn alloys of the present invention, regulated and controled by fixation rates, in finally making alloy substrate, even dispersion is distributed a large amount of hardening constituent, makes the Al-Mg alloy of the relatively conventional cold rolling state of alloy have bigger strength enhancing.Alloy of the present invention is highly suitable for exploitation and the production etc. further of plate armour and boats and ships aluminum alloy materials.
Detailed description of the invention
With reference now to the following examples, the present invention is described.
Being prepared for 9 kinds of alloys in laboratory scope, wherein alloy 1, alloy 2, alloy 4, alloy 5, alloy 6 and alloy 8 are with reference to alloy, alloy 3, alloy 7 and 3 embodiments that alloy 9 is the present invention.
Table 1 carries out an invention alloy composition table (mass percent, wt%)
The preparation method of the reference state H131 cold deformation state of alloy is as follows: after the smelting casting of alloy that will carry out an invention, start to be incubated 3~8h from room temperature to 425~440 DEG C with 20~40 DEG C/h heating rate, it is continuously heating to 500~535 DEG C of insulations 5~15h with 20~40 DEG C/h heating rate the most again, is cooled to room temperature with 20~40 DEG C/h rate of temperature fall with stove the most again.Sample being heated to 470~500 DEG C of insulation 2h, carries out the thermal deformation that deflection is more than 90%, finishing temperature is more than 380 DEG C.Sample is heated to 350~450 DEG C of insulations 0.5~2h, takes out air cooling.Then sample is carried out deflection be 10~30% cold roller and deformed.
The preparation method of twin-stage T6 Ageing Treatment state of the present invention is as follows: after the smelting casting of alloy that will carry out an invention, start to be incubated 3~8h from room temperature to 425~440 DEG C with 20~40 DEG C/h heating rate, it is continuously heating to 500~535 DEG C of insulations 5~15h with 20~40 DEG C/h heating rate the most again, is cooled to room temperature with 20~40 DEG C/h rate of temperature fall with stove the most again.Sample being heated to 470~500 DEG C of insulation 2h, carries out the thermal deformation that deflection is more than 90%, finishing temperature is more than 380 DEG C.Sample is heated to 350~450 DEG C of insulations 0.5~2h, takes out air cooling.Then sample is carried out deflection be 10~30% cold roller and deformed.Sample is incubated in the salt bath furnace of 500~535 DEG C 10~30min, then sample is directly carried out shrend.Sample is carried out in the heat-treatment furnace of 50~100 DEG C the first order Ageing Treatment of 12~36h, the most again 110~160 DEG C carry out 10~40h second level Ageing Treatment.
The mechanical property that measured alloy H131 Cold Rolled Strip and two-stage time effect separate out T6 state is as shown in table 2.
The mechanical property of the 2-in-1 gold of table
By table 2, all low than respective alloy H131 state with reference to alloy 1, alloy 2, alloy 4, alloy 5, alloy 6 and the tensile strength of alloy 8 two-stage time effect T6 state and yield strength;But tensile strength and yield strength ratio respective alloy H131 state by the two-stage time effect T6 state of the alloy 3 prepared by the present invention, alloy 7 and alloy 9 are high, and it has more excellent intensity and elongation percentage with existing compared with alloy.The sheet alloy that alloying component according to the present invention and preparation technology are obtained has the most excellent Precipitation strengthening effect.

Claims (6)

1. the preparation method of an Al-Mg-Zn system sheet alloy, it is characterised in that Al-Mg-Zn system alloy matter Amount degree is, 4.0~5.7%Mg, 2.5~4.0%Zn, 0~0.4%Cu, 0.4~1.2%Mn, 0~0.1%Cr, 0~0.15%Ti, 0.05~0.25%Zr, 0~0.4%Fe, 0~0.4%Si, remaining For Al;
Described preparation method comprises the following steps: melting and casting;Two-step homogenization is annealed;Hot rolling deformation;Middle Annealing;Cold roller and deformed;Solid solution and Water Quenching;Two-stage time effect processes;
The two-step homogenization annealing process of described aluminum alloy plate materials particularly as follows: by the alloy sample after melting and casting with The heating rate of 20~40 DEG C/h starts to be incubated 3~8h from room temperature to 425~440 DEG C, the most again with 20~ The heating rate of 40 DEG C/h is continuously heating to 500~535 DEG C of insulations 5~15h, the most again with 20~40 DEG C/h's Rate of temperature fall is cooled to room temperature with stove;
The hot rolling deformation technique of described aluminum alloy plate materials is incubated 2h particularly as follows: sample is heated to 470~500 DEG C, Carrying out the thermal deformation that deflection is more than 90%, finishing temperature is more than 380 DEG C.
The preparation method of Al-Mg-Zn system the most according to claim 1 sheet alloy, it is characterised in that institute State the intermediate annealing process of aluminum alloy plate materials particularly as follows: sample is heated to 350~450 DEG C insulation 0.5~ 2h, then air cooling.
The preparation method of Al-Mg-Zn system the most according to claim 1 sheet alloy, it is characterised in that institute State the cold roller and deformed technique of aluminum alloy plate materials particularly as follows: sample cold rolling reduction is 10~30%.
The preparation method of Al-Mg-Zn system the most according to claim 1 sheet alloy, it is characterised in that institute State the solid solution of aluminum alloy plate materials and Water Quenching technique particularly as follows: by sample at the salt bath of 500~535 DEG C Stove is incubated 10~30min, then sample is directly carried out shrend.
The preparation method of Al-Mg-Zn system the most according to claim 1 sheet alloy, it is characterised in that institute The two-stage time effect stating aluminum alloy plate materials processes technique particularly as follows: by sample the heat treatment of 50~100 DEG C Stove carries out the first order Ageing Treatment of 12~36h, carries out 10~40h at 110~160 DEG C the most again Second level Ageing Treatment.
The preparation method of Al-Mg-Zn system the most according to claim 1 sheet alloy, it is characterised in that institute Stating Al-Mg-Zn system alloy mass is, 4.3~5.5%Mg, 2.5~3.5%Zn, 0~0.2%Cu, 0.6~ 1.0%Mn, 0~0.1%Cr, 0~0.15%Ti, 0.05~0.25%Zr, 0~0.2%Fe, 0~0.2%Si, Remaining is Al.
CN201410577461.5A 2014-10-24 2014-10-24 A kind of Al-Mg-Zn system alloy and the preparation method of sheet alloy thereof CN104313413B (en)

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CN104862551B (en) * 2015-05-21 2017-09-29 北京科技大学 Al Mg Cu Zn line aluminium alloys and aluminum alloy plate materials preparation method
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CN108251666A (en) * 2018-02-01 2018-07-06 广西南南铝加工有限公司 A kind of preparation process of super high Mg-Al alloy plate
CN109898000B (en) * 2019-03-29 2020-12-15 郑州轻研合金科技有限公司 Ultrahigh-strength heat-resistant aluminum alloy and preparation method thereof
CN109930038B (en) * 2019-03-29 2020-12-29 北京科技大学 Thermomechanical treatment method for Al-Mg-Zn alloy plate
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