CN108330419A - A kind of thermal deformation of Al-Mg-Mn-Er-Zr sheet alloys and its stabilization process - Google Patents

A kind of thermal deformation of Al-Mg-Mn-Er-Zr sheet alloys and its stabilization process Download PDF

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Publication number
CN108330419A
CN108330419A CN201810219727.7A CN201810219727A CN108330419A CN 108330419 A CN108330419 A CN 108330419A CN 201810219727 A CN201810219727 A CN 201810219727A CN 108330419 A CN108330419 A CN 108330419A
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annealing
alloy
stabilization
deformation
carried
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CN201810219727.7A
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CN108330419B (en
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黄晖
谷鹏
聂祚仁
文胜平
高坤元
吴晓蓝
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北京工业大学
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    • 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
    • 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
    • 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

Abstract

A kind of thermal deformation of Al Mg Mn Er Zr sheet alloys and its stabilization process belong to non-ferrous alloy field, to Mg5.5% 6.5%;Mn0.7% 1.1%;Er0.1% 0.3%;Zr0.02% 0.12%;Fe < 0.4;Si < 0.4;Cu < 0.1;Zn < 0.2, surplus carry out hot rolling after being Al and the ingot casting progress two-step homogenization heat treatment of impurity, hot rolling technology is that trade time deformation of going forward side by side is heated at 250 350 DEG C, and mill speed is 0.1 0.3ms‑1.Gained hot rolled plate is subjected to 4 48h of stabilizing annealing at 240 300 DEG C.Gained alloy of the invention has higher intensity and preferable long-term corrosion resistance and the mechanical stability of long period.

Description

A kind of thermal deformation of Al-Mg-Mn-Er-Zr sheet alloys and its stabilization process

Technical field

The present invention relates to a kind of thermal deformation of Al-Mg-Mn-Er-Zr sheet alloys and its stabilization process, and belonging to has coloured gold Belong to technical field of alloy.

Technical background

5xxx line aluminium alloys are widely used in the fields such as traffic and transport due to its good corrosion resistance, with warp The development of Ji, more stringent requirements are proposed for intensity of the people to aluminium alloy.But alloy heat treatment can not be strengthened, and mainly pass through The means of solution strengthening, processing hardening and microalloying improve the comprehensive performance that this is alloy, and use state is cold deformation state Or annealed state etc..The intensity of aluminium alloy can be improved by improving the content of Mg;It is compounded to form by the way that the elements such as Er, Zr and matrix are added The heat safe second phase particles of disperse can improve the intensity and recrystallization temperature of alloy.When Mg contents are higher than in alloy When 3.5%, oversaturated Mg atoms can be precipitated in the base, be easy to form continuous netted β phases (Al3Mg2), alloy is in room temperature The tendency for the intercrystalline corrosion that happens occasionally is used for a long time.Traditional cold rolling adds stabilization process relatively complicated, and elongation percentage under The defects of drop, when cold rolling, are susceptible to crackle, and traditional hot rolling technology is not obvious the promotion of the strength of materials, and do not examine Test the long-term corrosion resistance of material.Therefore, make matrix that tiny disperse phase be precipitated by microalloying, then pass through controlled rolling Temperature and mill speed coordinate stabilizing annealing technique, material internal can be made to form more subgrain tissue, to be bent Intensity, elongation percentage and the good high Mg-Al alloy plate containing Er of long-term corrosion resistance are taken, it is domestic at present to be closed to containing Er high magnaliums The technique of the thermal deformation of golden plate material and stabilizing annealing rarely has introduction.

Invention content

Present invention aims at provide a kind of Al-Mg-Mn-Er-Zr sheet alloys suitable for high magnesium thermal deformation and its Stabilization process makes matrix that tiny disperse phase be precipitated, then by rolling temperature control and mill speed, matches by microalloying Stabilizing annealing technique is closed, material internal can be made to form more subgrain tissue, to obtain yield strength, elongation percentage and length The good high Mg-Al alloy plate containing Er of phase corrosion resistance.

The thermal deformation of Al-Mg-Mn-Er-Zr sheet alloys provided by the invention and its stabilization process, including following step Suddenly:

(1) to Mg, 5.5%-6.5%;Mn, 0.7%-1.1%;Er, 0.1%-0.3%;Zr, 0.02%-0.12%;Fe < 0.4;Si < 0.4;Cu < 0.1;Zn < 0.2, surplus is Al and the almag of inevitable impurity (above-mentioned is quality percentage Than content) ingot casting carry out 280 ± 10 DEG C/10h heat preservation, then rise to 450 ± 10 DEG C heat preservation for 24 hours two-step homogenization annealing after heat It rolls, hot rolling technology is that trade time deformation of going forward side by side, mill speed 0.1-0.3ms are heated at 250-350 DEG C-1, it is air-cooled to room Temperature;;

(2) stabilizing annealing is carried out at 240-300 DEG C through the deformed hot rolled plate of step (1) passage, annealing time is 4-48h.It is air-cooled to room temperature.

Beneficial effects of the present invention:

The second tiny phase of disperse is formed by compound addition Er, Zr and homogenization, the intensity of alloy is improved and ties again Brilliant finishing temperature coordinates stabilizing annealing technique by rolling temperature control, mill speed, forms Asia that is more and stablizing Crystalline substance tissue, avoids the continuous precipitation of β phases, good containing Er to obtain yield strength, elongation percentage and long-term corrosion resistance High Mg-Al alloy plate.

Description of the drawings

The Al being precipitated in 3 alloy structure of Fig. 1 embodiments3Er phases

The β phases being discontinuously precipitated in alloy grain boundaries in Fig. 2 embodiments 3.

Specific implementation mode

The following contents is that the invention will be further described in conjunction with the embodiments, but the present invention is not limited to following embodiments.Table 1 Alloy hot plank stabilizing annealing post-tensioning performance

2 alloy hot plank stabilizing annealing post-etching performance of table

3 comparative example alloy hot plate stretch performance of table

4 comparative example alloy hot plank corrosive nature of table

Embodiment 1:

1) to mass percentage:Mg, 5.9%;Mn, 0.84%;Er, 0.2%;Zr, 0.09%;Fe < 0.4;Si < 0.4;Cu < 0.1;Zn < 0.2, surplus are the almag of Al and inevitable impurity, and 280 DEG C/10h heat preservations are carried out to ingot casting, After rising to the two-step homogenization annealing of 450 DEG C of heat preservations for 24 hours again, 2h is kept the temperature at 250 DEG C, and passage change is carried out under holding temperature Shape, reduction in pass 30%, mill speed 0.1ms-1, it is air-cooled to room temperature.

2) to carrying out stabilizing annealing, annealing time 48h at 240 DEG C through hot rolled plate obtained by step 1).It is air-cooled to room Temperature.Tensile property test is carried out to the plank after stabilisation, and quick to alloy according to Unite States Standard ASTM G66 and ASTM G67 Intercrystalline corrosion and Peeling Corrosion before and after change (100 DEG C/7 days) are tested.Tensile property is shown in Table 1, and corrosive nature is shown in Table 2.

Comparative example 1:

1) to mass percentage:Mg, 5.9%;Mn, 0.84%;Er, 0.2%;Zr, 0.09%;Fe < 0.4;Si < 0.4;Cu < 0.1;Zn < 0.2, surplus are the almag of Al and inevitable impurity, and 280 DEG C/10h heat preservations are carried out to ingot casting, After rising to the two-step homogenization annealing of 450 DEG C of heat preservations for 24 hours again, 2h is kept the temperature at 250 DEG C, and passage change is carried out under holding temperature Shape, reduction in pass 30%, mill speed 0.1ms-1, it is air-cooled to room temperature.

2) tensile property test is carried out to plank, and alloy is sensitized according to Unite States Standard ASTM G66 and ASTM G67 Intercrystalline corrosion and Peeling Corrosion before and after (100 DEG C/7 days) are tested.Tensile property is shown in Table 1, and corrosive nature is shown in Table 2.

Embodiment 2:

1) to mass percentage:Mg, 5.9%;Mn, 0.84%;Er, 0.2%;Zr, 0.09%;Fe < 0.4;Si < 0.4;Cu < 0.1;Zn < 0.2, surplus are the almag of Al and inevitable impurity, and 280 DEG C/10h heat preservations are carried out to ingot casting, After rising to the two-step homogenization annealing of 450 DEG C of heat preservations for 24 hours again, 2h is kept the temperature at 300 DEG C, and passage change is carried out under holding temperature Shape, reduction in pass 30%, mill speed 0.1ms-1, it is air-cooled to room temperature.

2) to carrying out stabilizing annealing, annealing time 10h at 260 DEG C through hot rolled plate obtained by step 1).It is air-cooled to room Temperature.Tensile property test is carried out to the plank after stabilisation, and quick to alloy according to Unite States Standard ASTM G66 and ASTM G67 Intercrystalline corrosion and Peeling Corrosion before and after change (100 DEG C/7 days) are tested.Tensile property is shown in Table 1, and corrosive nature is shown in Table 2.

Comparative example 2:

1) to mass percentage:Mg, 5.9%;Mn, 0.84%;Er, 0.2%;Zr, 0.09%;Fe < 0.4;Si < 0.4;Cu < 0.1;Zn < 0.2, surplus are the almag of Al and inevitable impurity, and 280 DEG C/10h heat preservations are carried out to ingot casting, After rising to the two-step homogenization annealing of 450 DEG C of heat preservations for 24 hours again, 2h is kept the temperature at 300 DEG C, and passage change is carried out under holding temperature Shape, reduction in pass 30%, mill speed 0.1ms-1, it is air-cooled to room temperature.

2) tensile property test is carried out to plank, and alloy is sensitized according to Unite States Standard ASTM G66 and ASTM G67 Intercrystalline corrosion and Peeling Corrosion before and after (100 DEG C/7 days) are tested.Tensile property is shown in Table 1, and corrosive nature is shown in Table 2.

Embodiment 3:

1) to mass percentage:Mg, 5.9%;Mn, 0.84%;Er, 0.2%;Zr, 0.09%;Fe < 0.4;Si < 0.4;Cu < 0.1;Zn < 0.2, surplus are the almag of Al and inevitable impurity, and 280 DEG C/10h heat preservations are carried out to ingot casting, After rising to the two-step homogenization annealing of 450 DEG C of heat preservations for 24 hours again, 2h is kept the temperature at 350 DEG C, and passage change is carried out under holding temperature Shape, reduction in pass 30%, mill speed 0.1ms-1, it is air-cooled to room temperature.

2) to carrying out stabilizing annealing, annealing time 6h at 280 DEG C through hot rolled plate obtained by step 1).It is air-cooled to room Temperature.Tensile property test is carried out to the plank after stabilisation, and quick to alloy according to Unite States Standard ASTM G66 and ASTM G67 Intercrystalline corrosion and Peeling Corrosion before and after change (100 DEG C/7 days) are tested.Tensile property is shown in Table 1, and corrosive nature is shown in Table 2.

Comparative example 3:

1) to mass percentage:Mg, 5.9%;Mn, 0.84%;Er, 0.2%;Zr, 0.09%;Fe < 0.4;Si < 0.4;Cu < 0.1;Zn < 0.2, surplus are the almag of Al and inevitable impurity, and 280 DEG C/10h heat preservations are carried out to ingot casting, After rising to the two-step homogenization annealing of 450 DEG C of heat preservations for 24 hours again, 2h is kept the temperature at 350 DEG C, and passage change is carried out under holding temperature Shape, reduction in pass 30%, mill speed 0.1ms-1, it is air-cooled to room temperature.

2) tensile property test is carried out to plank, and alloy is sensitized according to Unite States Standard ASTM G66 and ASTM G67 Intercrystalline corrosion and Peeling Corrosion before and after (100 DEG C/7 days) are tested.Tensile property is shown in Table 1, and corrosive nature is shown in Table 2.

Embodiment 4:

1) to mass percentage:Mg, 5.9%;Mn, 0.84%;Er, 0.2%;Zr, 0.09%;Fe < 0.4;Si < 0.4;Cu < 0.1;Zn < 0.2, surplus are the almag of Al and inevitable impurity, and 280 DEG C/10h heat preservations are carried out to ingot casting, After rising to the two-step homogenization annealing of 450 DEG C of heat preservations for 24 hours again, 2h is kept the temperature at 350 DEG C, and passage change is carried out under holding temperature Shape, reduction in pass 30%, mill speed 0.1ms-1, it is air-cooled to room temperature.

2) to carrying out stabilizing annealing, annealing time 4h at 300 DEG C through hot rolled plate obtained by step 1).It is air-cooled to room Temperature.Tensile property test is carried out to the plank after stabilisation, and quick to alloy according to Unite States Standard ASTM G66 and ASTM G67 Intercrystalline corrosion and Peeling Corrosion before and after change (100 DEG C/7 days) are tested.Tensile property is shown in Table 1, and corrosive nature is shown in Table 2.

1 alloy hot plank stabilizing annealing post-tensioning performance of table

2 alloy hot plank stabilizing annealing post-etching performance of table

3 comparative example alloy hot plate stretch performance of table

4 comparative example alloy hot plank corrosive nature of table

By Tables 1 and 2 it is found that the extension of the raising and annealing time with step (2) Annealing Temperature, alloy Yield strength and tensile strength decrease, and elongation percentage is increased and tended towards stability.When different conditions warm deformation alloy is through steady When yield strength is less than 240MPa after fixedization, the elongation percentage of alloy and resistance to long-term corrosion better performances.

For alloy after Homogenization Treatments, the tiny disperse phase of precipitation improves the recrystallization finishing temperature of alloy, hinders Recrystallization when subsequent heat treatment.The resistance of deformation of alloy material internal when carrying out warm deformation is smaller, different temperatures deformation The main mechanism that Shi Hejin softens is that different degrees of dynamic recovery has occurred, and material internal generates more subgrain group It knits.Stabilizing annealing is carried out to plank, the internal stress of alloy can be eliminated, and promotes β phases uniformly disconnected in transgranular and crystal boundary etc. Continuous precipitation, improves the resistance to corrosion of alloy, and the long-term corrosion resistance of alloy is preferable.

Claims (2)

  1. The thermal deformation of 1.Al-Mg-Mn-Er-Zr sheet alloys and its stabilization process, which is characterized in that include the following steps:
    (1) to Mg, 5.5%-6.5%;Mn, 0.7%-1.1%;Er, 0.1%-0.3%;Zr, 0.02%-0.12%;Fe < 0.4;Si < 0.4;Cu < 0.1;Zn < 0.2, surplus is Al and the almag of inevitable impurity (above-mentioned is mass percent Content) ingot casting carry out 280 ± 10 DEG C/10h heat preservation, then rise to 450 ± 10 DEG C heat preservation for 24 hours two-step homogenization annealing after heat It rolls, hot rolling technology is that trade time deformation of going forward side by side, mill speed 0.1-0.3ms are heated at 250-350 DEG C-1, it is air-cooled to room temperature;
    (2) stabilizing annealing, annealing time 4- are carried out at 240-300 DEG C through the deformed hot rolled plate of step (1) passage 48h;It is air-cooled to room temperature.
  2. 2. thermal deformation and its stabilization process of Al-Mg-Mn-Er-Zr sheet alloys described in accordance with the claim 1, feature It is, heated at 250 DEG C -350 DEG C after step (1) homogenizing annealing and carries out passage deformation at the heating temperature;Through step Suddenly the deformed hot rolled plate of (1) passage carries out stabilizing annealing, annealing time 4-48h at 240-300 DEG C.
CN201810219727.7A 2018-03-16 2018-03-16 Thermal deformation and stabilization process of Al-Mg-Mn-Er-Zr alloy plate CN108330419B (en)

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Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109022954A (en) * 2018-09-14 2018-12-18 东北轻合金有限责任公司 A kind of aluminium alloy strips and its manufacturing method of spiral welded pipe
CN109680192A (en) * 2019-01-29 2019-04-26 北京工业大学 A kind of Al-Mg-Mn-Er-Zr alloy hot and stabilizing annealing technique and material
CN109735749A (en) * 2019-01-17 2019-05-10 北京工业大学 A kind of alloy hot rolled stabilizing annealing technique of Al-Mg-Mn-Er-Zr
CN110760723A (en) * 2019-07-19 2020-02-07 北京工业大学 Aluminum-magnesium-silicon-erbium-zirconium alloy and preparation process for improving high-temperature mechanical property
CN111155003A (en) * 2020-02-25 2020-05-15 广西大学 High-strength high-toughness high-magnesium aluminum alloy and preparation method thereof

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2002256364A (en) * 2001-02-28 2002-09-11 Mitsubishi Alum Co Ltd Aluminum alloy for fin material of fin for heat exchanger and its production method
JP2011058047A (en) * 2009-09-10 2011-03-24 Furukawa-Sky Aluminum Corp Method for producing aluminum alloy thick plate having excellent strength and ductility
CN102534322A (en) * 2012-01-06 2012-07-04 北京工业大学 Process for strengthening temperature deformation of Er-containing aluminum-magnesium alloy sheet material
CN105177327A (en) * 2015-09-11 2015-12-23 广西南南铝加工有限公司 Preparation method for high-magnesium aluminum alloy O-state plate of 5XXX series

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2002256364A (en) * 2001-02-28 2002-09-11 Mitsubishi Alum Co Ltd Aluminum alloy for fin material of fin for heat exchanger and its production method
JP2011058047A (en) * 2009-09-10 2011-03-24 Furukawa-Sky Aluminum Corp Method for producing aluminum alloy thick plate having excellent strength and ductility
CN102534322A (en) * 2012-01-06 2012-07-04 北京工业大学 Process for strengthening temperature deformation of Er-containing aluminum-magnesium alloy sheet material
CN105177327A (en) * 2015-09-11 2015-12-23 广西南南铝加工有限公司 Preparation method for high-magnesium aluminum alloy O-state plate of 5XXX series

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109022954A (en) * 2018-09-14 2018-12-18 东北轻合金有限责任公司 A kind of aluminium alloy strips and its manufacturing method of spiral welded pipe
CN109735749A (en) * 2019-01-17 2019-05-10 北京工业大学 A kind of alloy hot rolled stabilizing annealing technique of Al-Mg-Mn-Er-Zr
CN109680192A (en) * 2019-01-29 2019-04-26 北京工业大学 A kind of Al-Mg-Mn-Er-Zr alloy hot and stabilizing annealing technique and material
CN110760723A (en) * 2019-07-19 2020-02-07 北京工业大学 Aluminum-magnesium-silicon-erbium-zirconium alloy and preparation process for improving high-temperature mechanical property
CN111155003A (en) * 2020-02-25 2020-05-15 广西大学 High-strength high-toughness high-magnesium aluminum alloy and preparation method thereof

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