CN104046855A - Manufacturing method of bending-resistant high-strength aluminium magnesium alloy - Google Patents
Manufacturing method of bending-resistant high-strength aluminium magnesium alloy Download PDFInfo
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- CN104046855A CN104046855A CN201310083769.XA CN201310083769A CN104046855A CN 104046855 A CN104046855 A CN 104046855A CN 201310083769 A CN201310083769 A CN 201310083769A CN 104046855 A CN104046855 A CN 104046855A
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Abstract
The invention relates to a manufacturing method of bending-resistant high-strength aluminium magnesium alloy, comprising the following steps: (a) aluminium blank casting: 4-4.9 wt% of magnesium, less than 0.2 wt% of silicon, less than 0.35wt% of iron, less than 0.15 wt% of copper, 0.2-0.5 wt% of manganese, less than 0.1 wt% of chromium, less than 0.25 wt% of zinc, less than 0.1wt% of titanium, less than 0.15 wt% of unavoidable impurities and the balance aluminium and other elements undergo fusion and casting to form an aluminium blank; (b) preheating of the aluminium blank; (c) hot rolling of the aluminium blank; (d) first cold rolling of the aluminium blank; (e) intermediate annealing treatment of the aluminium blank for perfect recrystallization and softening of the aluminium blank; (f) second cold rolling of the aluminium blank; and (g) final annealing heat treatment of the aluminium blank for formation of the bending-resistant high-strength aluminium magnesium alloy.
Description
[technical field]
The present invention relates to a kind of alloy manufacture method, particularly a kind of resistance to bending high-strength aluminium-magnesium alloy manufacture method.
[prior art]
Known process sclerotic type magnalium (Al-Mg) alloy, because having good intensity and anodizing performance, is widely used in the 3C industry of compact demand.When known manufacture aluminum magnesium alloy, metropolitan adopts the method that increases magnesium (Mg) addition, makes aluminium produce work strengthening effect cold rolling in prolonging process, to increase aluminium intensity.But, above-mentioned via aluminium alloy (the commercial H1n that is called after cold rolling, containing H12, H14, H16, H18 and H19), although have high strength, but because of (the Yield Strength of the yield strength in material behavior, be called for short Y.S.) and tensile strength (Tensile Strength, being called for short T.S.) ratio is high, make aluminum magnesium alloy in forming process, once deflection exceedes elastic range (being Y.S. point) and enters plastically deforming area, just can easily exceed T.S. point, cause constriction (Necking) phenomenon to occur ahead of time, that is aluminum magnesium alloy will be for want of ductility (or elongation) and fracture fast.
Therefore, general aluminium manufacturer, in order to increase the ductility of high-strength aluminium-magnesium alloy, is the most often used the processing procedure of H3n and two kinds of tempers of H2n, and its processing procedure is summarized as follows:
(1) H3n processing procedure: to the aluminum magnesium alloy after cold rolling, bestow again 150 to 180 DEG C of annealing thermal treatments, utilize this kind of reply (Recovery) annealing process, reduce dislocation (Dislocation) density in aluminum magnesium alloy, to reduce Y.S./T.S. ratio, reach and increase the elongation of aluminium alloy and the object of processing characteristics.
(2) H2n processing procedure: and the comparison of H3n processing procedure, H2n processing procedure, without process annealing processing procedure, is direct cold rolling method, has the advantage of accelerating Production Flow Chart, saving manufacturing cost.It is to utilize final annealing thermal treatment equally, reduces dislocation (Dislocation) density in aluminum magnesium alloy, to reduce Y.S./T.S. ratio, reaches and increases the elongation of aluminium alloy and the object of processing characteristics.
In addition, learn that by above-mentioned processing procedure Mg content exceedes the above aluminum magnesium alloy of 3 % by weight (for example 5086,5083,5456 and 5182 etc. type aluminum magnesium alloy), if expose to the open air for a long time or be under 66 to 180 DEG C of Working environments in room temperature, capital impels β (Mg2A13) to separate out on crystal boundary, and along with exposure duration is more of a specified duration, its amount of separating out is larger.Have more positive polarity because β compares aluminum magnesium alloy, therefore, will cause mutually aluminum magnesium alloy to be easily damaged by corrosion once β appears in crystal boundary.In addition, when crystal boundary has fine and closely woven precipitate, more easily cause boundary segregation and reduce the ductility of aluminum magnesium alloy, because precipitate hardness is often higher than alloy material itself, and not good with alloy material adaptation, therefore in forming process, microscopic checks the most easily originates in grain boundary precipitate periphery, and then propagate along crystal boundary, cause alloy material to be shaped and break unsuccessfully.
In addition, from H3n processing procedure, 150 to 180 DEG C of recovery annealing thermal treatments, will impel β to separate out on aluminum magnesium alloy crystal boundary, it cannot solve the forming property of the aluminum magnesium alloy of high Mg content (being greater than 4 % by weight) completely, the thermal treatment of even annealing is improper, also can reduce the etch resistant properties of alloy material.
In view of this, be necessary to provide the resistance to bending high-strength aluminium-magnesium alloy manufacture method of an innovation and tool progressive, to address the above problem.
[summary of the invention]
The invention provides a kind of resistance to bending high-strength aluminium-magnesium alloy manufacture method, comprise the following steps: (a) carry out an aluminium embryo casting step, by the manganese of the magnesium of 4 to 4.9 % by weight, the silicon that is less than 0.2 % by weight, the iron that is less than 0.35 % by weight, the copper that is less than 0.15 % by weight, 0.2 to 0.5 % by weight, be less than 0.1 % by weight chromium, be less than 0.25 % by weight zinc, be less than 0.1 % by weight titanium, be less than the element melting such as unavoidable impurity and the aluminium of all the other of 0.15 % by weight and be cast into an aluminium embryo; (b) this aluminium embryo of preheating; (c) this aluminium embryo is prolonged in hot rolling; (d) this aluminium embryo is carried out to cold rolling prolonging for the first time; (e) this aluminium embryo is carried out to process annealing thermal treatment, so that this aluminium embryo perfect recrystallization and softening; (f) this aluminium embryo is carried out to cold rolling prolonging for the second time; And (g) this aluminium embryo is carried out to final annealing thermal treatment, to form this resistance to bending high-strength aluminium-magnesium alloy.
The present invention uses the low cold rolling amount of prolonging processing procedure, make Mg content exceed the above aluminum magnesium alloy inside of 4 % by weight and have suitable strain energy, therefore in subsequent anneal heat treatment process, aluminium embryo Strength Changes is more insensitive to annealing temperature height, therefore in the time that batch mode of employing is produced, the aluminium of 20 to 30 tons of weights of whole heat is rolled up except obtaining more even mechanical properties, also because exceeding crystal boundary β-Mg2A13, final annealing temperature the most easily separates out mutually scope (66 to 180 DEG C), therefore the bending forming that is difficult for occurring in similar traditional H3n processing procedure breaks or corrosion phenomenon.
[brief description of the drawings]
Fig. 1 shows the resistance to bending high-strength aluminium-magnesium alloy manufacture method schema of the present invention.
[embodiment]
Fig. 1 shows the resistance to bending high-strength aluminium-magnesium alloy manufacture method schema of the present invention.Refer to the step S11 of Fig. 1, carry out an aluminium embryo casting step, by the magnesium of 4 to 4.9 % by weight, be less than the silicon of 0.2 % by weight, be less than the iron of 0.35 % by weight, be less than the copper of 0.15 % by weight, the manganese of 0.2 to 0.5 % by weight, be less than the chromium of 0.1 % by weight, be less than the zinc of 0.25 % by weight, be less than the titanium of 0.1 % by weight, be less than the unavoidable impurity of 0.15 % by weight and the elements such as the aluminium mutual melting of high temperature more than 700 DEG C of all the other, through degasification, after deslagging filtering and the thin brilliant agent of interpolation, be cast into an aluminium embryo with a direct chill casting (Direct Chill Casting) equipment.
Refer to step S12, this aluminium embryo of preheating, in this step, preheating temperature is not less than 480 DEG C.
Refer to step S13, this aluminium embryo is prolonged in hot rolling, in this step, the aluminum magnesium alloy above because of Mg content 4 % by weight belongs to high work strengthening type aluminium alloy, therefore temperature is prolonged in hot rolling must be between 300 to 480 DEG C, otherwise too low hot rolling is prolonged temperature and will be caused aluminium embryo to prolong and in process, produce serious limit and split phenomenon in hot rolling.
Refer to step S14, this aluminium embryo is carried out to cold rolling prolonging for the first time.
Refer to step S15, this aluminium embryo is carried out to process annealing thermal treatment, so that this aluminium embryo perfect recrystallization and softening.This process annealing thermal treatment is mainly to allow aluminium flake reach dead annealed soft state (the O temper temper being commonly called as), therefore, to annealing temperature and have no special requirements, generally aluminium alloy production plant, can be depending on the heat-treatable aluminum alloy amount of this heat, process annealing thermal treatment temp can exceed 280 DEG C conventionally.
Refer to step S16, this aluminium embryo is carried out to cold rolling prolonging for the second time, in this step, aluminium embryo reduced thickness amount (Reduction) must be strict controlled between 25 to 40%, this measure can be in the suitable cold working dislocation (Dislocation) of the inner intervention of aluminium, so that aluminum magnesium alloy has high-intensity performance.In addition, the cold working dislocation amount in above-mentioned scope, more insensitive to the variation of annealing temperature height, therefore, can make follow-up final annealing thermal treatment temp have the execution scope of broadness.
Refer to step S17, this aluminium embryo is carried out to final annealing thermal treatment, to form this resistance to bending high-strength aluminium-magnesium alloy.In this step, annealing heat treatment time is between 2 to 5 hours, and annealing thermal treatment temp is between 210 to 250 DEG C, the most easily separate out mutually scope to avoid crystal boundary β between 66 to 180 DEG C-Mg2A13, so, the aluminum magnesium alloy that can make to be formed has the advantages such as resistance to bending (high elongation rate), high strength, final annealing temperature range be wide and not perishable, and wherein the elongation of this resistance to bending high-strength aluminium-magnesium alloy is not less than 10%, and yield strength is not less than 210MPa.
Hereby describe the present invention in detail with the following example, but the present invention is not limited to the disclosed content of these embodiment.
The Chemical Composition that table 1 is aluminum magnesium alloy embodiment of the present invention, magnesium adds the work strengthening and the strength demand that are mainly intended to increase material, magnesium elements addition is 4.6 % by weight, this is worth far above 3 % by weight, therefore it is very responsive that annealing thermal treatment processing procedure is separated out mutually to crystal boundary β-Mg2A13, careless slightly easily cause being shaped destroy.
The Chemical Composition (% by weight) of table 1. aluminum magnesium alloy embodiment of the present invention
| Silicon (Si) | Iron (Fe) | Copper (Cu) | Manganese (Mn) | Magnesium (Mg) | Chromium (Cr) | Zinc (Zn) | Titanium (Ti) | Aluminium (Al) |
| 0.12 | 0.24 | 0.02 | 0.23 | 4.4 | 0.03 | 0.004 | 0.011 | All the other |
Table 2 is the test result of the every capability and performance of embodiment.Test piece 1 shows that aluminum magnesium alloy is through after 35% cold rolling amount for the second time, when without any final annealing thermal treatment, its yield strength (Y.S.) all exceedes 400MPa with tensile strength values (T.S.), and because Y.S./T.S. ratio is up to 0.95, and elongation only has 6.5%, do not reach the requirement that general bending is shaped to material percentage elongation lower value 10%, therefore bending forming breaks.2 of test pieces are manufactured according to program of the present invention completely, by the test piece 1 240 DEG C of final annealing heat treatment steps together that apply again more, can observe except elongation has exceeded 10% and reach 13.5%, Y.S./T.S. is down to 0.70 than also thereupon, therefore has good bending forming performance.Although 3 of test pieces highlight the scope that cold rolling amount for the second time meets the present invention, if but final annealing thermal treatment selection is improper, for example select 180 DEG C, except Y.S./T.S. reaches 0.80 than still higher, elongation is also lower than 10% requirement, in addition,, owing to the most easily separating out mutually scope (240 DEG C) thermal treatment at crystal boundary β-Mg2A13, will cause the formation in crack in bending forming process and fast propagation and rupture.
The test result of the every capability and performance of table 2. embodiment
Note: crooked test is 90 degree 0t
For proving that the present invention has broader practicality, will be for the second time cold rolling amount be reduced to 27% from 35%, and no matter final annealing temperature is 210 DEG C or 240 DEG C of high temperature that adopt low temperature, all has good intensity and brake forming performance.From table 2 data, carry out test piece 2, test piece 4 and test piece 5 threes relatively, more can find that no matter three is in intensity, elongation, Y.S./T.S. ratio or bend test results, all very approaching, proved is invented in aluminium alloy production application, has the advantage of sizable operating restraint and quality uniformity.But, if cold rolling amount exceedes 40% for the second time, for example adopt 67% high cold rolling amount, from the metallurgical viewpoint of material, the higher expression material of cold rolling amount is subject to external force machining deformation amount more, therefore material internal also just has high strain energy, and easier excitation material, in annealing heat treatment process moment, recrystallize and soften is occurred to, this phenomenon can be from table 2 test piece 6 and the every test data comparative observation of test piece 7 to.
Test piece 6 shows the aluminum magnesium alloy cold rolling through 67%, and in the time carrying out final annealing thermal treatment for 230 DEG C, Y.S. value is still up to 279MPa, and Y.S./T.S. is more higher than also, causes bending to be broken.Test piece 7 is for to be increased to a little 240 DEG C by the final annealing heat-treat condition of test piece 6, although can test by bending forming, so Y.S. value is but because moment is softened fast-descending to 189MPa, cannot reach Y.S. value higher than the above requirement of 210MPa, for aluminium alloy factory, the cold rolling processing procedure of this kind 67%, the H18 of the most often employing of similar aluminium alloy factory or H2n temper processing procedure, wish to promote the strength of materials by the cold rolling amount of height, but because it is quite responsive to final annealing temperature height to be limited to aluminium flake intensity, and cannot produce the aluminium alloy that quality is even.Above-described embodiment confirms to meet the present invention's method parameter, can produce the aluminum magnesium alloy that quality is even.
Above-described embodiment is only for principle and effect thereof of the present invention are described, and unrestricted the present invention, and therefore those skilled in the art modify to above-described embodiment and change the spirit that does not still take off the present invention.The present invention's interest field should be as listed in claims.
Claims (8)
1. a resistance to bending high-strength aluminium-magnesium alloy manufacture method, comprises the following steps:
(a) carry out an aluminium embryo casting step, by the manganese of the magnesium of 4 to 4.9 % by weight, the silicon that is less than 0.2 % by weight, the iron that is less than 0.35 % by weight, the copper that is less than 0.15 % by weight, 0.2 to 0.5 % by weight, be less than 0.1 % by weight chromium, be less than 0.25 % by weight zinc, be less than 0.1 % by weight titanium, be less than the element melting such as unavoidable impurity and the aluminium of all the other of 0.15 % by weight and be cast into an aluminium embryo;
(b) this aluminium embryo of preheating;
(c) this aluminium embryo is prolonged in hot rolling;
(d) this aluminium embryo is carried out to cold rolling prolonging for the first time;
(e) this aluminium embryo is carried out to process annealing thermal treatment, so that this aluminium embryo perfect recrystallization and softening;
(f) this aluminium embryo is carried out to cold rolling prolonging for the second time; And
(g) this aluminium embryo is carried out to final annealing thermal treatment, to form this resistance to bending high-strength aluminium-magnesium alloy.
2. the process of claim 1 wherein that the preheating temperature of step (b) is not less than 480 DEG C.
3. the process of claim 1 wherein that the hot rolling of step (c) prolongs temperature between 300 to 480 DEG C.
4. the process of claim 1 wherein that the aluminium embryo reduced thickness amount of step (f) is between 25 to 40%.
5. the process of claim 1 wherein that the annealing thermal treatment temp of step (g) is between 210 to 250 DEG C.
6. the process of claim 1 wherein that the annealing heat treatment time of step (g) is between 2 to 5 hours.
7. the process of claim 1 wherein that the yield strength of this resistance to bending high-strength aluminium-magnesium alloy of being formed is not less than 210MPa.
8. the process of claim 1 wherein that the elongation of this resistance to bending high-strength aluminium-magnesium alloy of being formed is not less than 10%.
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| CN201310083769.XA CN104046855A (en) | 2013-03-15 | 2013-03-15 | Manufacturing method of bending-resistant high-strength aluminium magnesium alloy |
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106435297A (en) * | 2016-11-17 | 2017-02-22 | 东莞宜安科技股份有限公司 | Preparation method for bending-resistant and corrosion-resistant high-strength aluminium magnesium alloy and product thereof |
| CN106521261A (en) * | 2016-11-17 | 2017-03-22 | 东莞宜安科技股份有限公司 | Method used for preparing high-strength corrosion-resistant aluminium magnesium alloy sheets, and products and applications of high-strength corrosion-resistant aluminium magnesium alloy sheets |
| CN111485148A (en) * | 2020-04-03 | 2020-08-04 | 河南中孚高精铝材有限公司 | Novel alloy plate meeting special comprehensive mechanical property requirements and preparation method thereof |
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| JPH01301831A (en) * | 1988-05-31 | 1989-12-06 | Kobe Steel Ltd | Al alloy plate for stay-on tab and its manufacture |
| JPH01312054A (en) * | 1988-06-13 | 1989-12-15 | Kobe Steel Ltd | Aluminum alloy for magnetic disk and its production |
| JPH04176837A (en) * | 1990-11-09 | 1992-06-24 | Furukawa Alum Co Ltd | Aluminum alloy material for forming excellent in bendability, corrosion resistance and spring property and its manufacture |
| JPH1161311A (en) * | 1997-08-28 | 1999-03-05 | Nippon Steel Corp | Aluminum alloy sheet for car body panel and its production |
| CN1643172A (en) * | 2002-03-22 | 2005-07-20 | 皮奇尼何纳吕公司 | Al-Mg alloy products for a welded construction |
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Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH01301831A (en) * | 1988-05-31 | 1989-12-06 | Kobe Steel Ltd | Al alloy plate for stay-on tab and its manufacture |
| JPH01312054A (en) * | 1988-06-13 | 1989-12-15 | Kobe Steel Ltd | Aluminum alloy for magnetic disk and its production |
| JPH04176837A (en) * | 1990-11-09 | 1992-06-24 | Furukawa Alum Co Ltd | Aluminum alloy material for forming excellent in bendability, corrosion resistance and spring property and its manufacture |
| JPH1161311A (en) * | 1997-08-28 | 1999-03-05 | Nippon Steel Corp | Aluminum alloy sheet for car body panel and its production |
| CN1643172A (en) * | 2002-03-22 | 2005-07-20 | 皮奇尼何纳吕公司 | Al-Mg alloy products for a welded construction |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106435297A (en) * | 2016-11-17 | 2017-02-22 | 东莞宜安科技股份有限公司 | Preparation method for bending-resistant and corrosion-resistant high-strength aluminium magnesium alloy and product thereof |
| CN106521261A (en) * | 2016-11-17 | 2017-03-22 | 东莞宜安科技股份有限公司 | Method used for preparing high-strength corrosion-resistant aluminium magnesium alloy sheets, and products and applications of high-strength corrosion-resistant aluminium magnesium alloy sheets |
| CN111485148A (en) * | 2020-04-03 | 2020-08-04 | 河南中孚高精铝材有限公司 | Novel alloy plate meeting special comprehensive mechanical property requirements and preparation method thereof |
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Application publication date: 20140917 |