CN104152826B - A kind of heat treatment method of Mg-Al-Zn-Y magnesium-rare earth - Google Patents
A kind of heat treatment method of Mg-Al-Zn-Y magnesium-rare earth Download PDFInfo
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- CN104152826B CN104152826B CN201410340276.4A CN201410340276A CN104152826B CN 104152826 B CN104152826 B CN 104152826B CN 201410340276 A CN201410340276 A CN 201410340276A CN 104152826 B CN104152826 B CN 104152826B
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- 229910052761 rare earth metal Inorganic materials 0.000 title claims abstract description 55
- 238000010438 heat treatment Methods 0.000 title claims abstract description 20
- 238000000034 method Methods 0.000 title claims abstract description 19
- 238000001125 extrusion Methods 0.000 claims abstract description 20
- 238000001816 cooling Methods 0.000 claims abstract description 15
- 238000001192 hot extrusion Methods 0.000 claims abstract description 12
- 238000005266 casting Methods 0.000 claims abstract description 11
- 239000000463 material Substances 0.000 claims abstract description 10
- 229910052725 zinc Inorganic materials 0.000 claims abstract description 3
- 238000009413 insulation Methods 0.000 claims 1
- 150000002910 rare earth metals Chemical class 0.000 abstract description 7
- 239000013078 crystal Substances 0.000 abstract description 5
- 238000002161 passivation Methods 0.000 abstract description 3
- 239000000470 constituent Substances 0.000 abstract description 2
- 239000002244 precipitate Substances 0.000 abstract description 2
- 229910045601 alloy Inorganic materials 0.000 description 16
- 239000000956 alloy Substances 0.000 description 16
- 229910000861 Mg alloy Inorganic materials 0.000 description 10
- 230000000694 effects Effects 0.000 description 10
- 239000011777 magnesium Substances 0.000 description 8
- 230000032683 aging Effects 0.000 description 6
- 238000001556 precipitation Methods 0.000 description 6
- 238000009826 distribution Methods 0.000 description 5
- 239000006104 solid solution Substances 0.000 description 5
- 238000005728 strengthening Methods 0.000 description 5
- 238000001953 recrystallisation Methods 0.000 description 4
- 239000000243 solution Substances 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 3
- 238000002425 crystallisation Methods 0.000 description 2
- 230000008025 crystallization Effects 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 210000001787 dendrite Anatomy 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 239000008187 granular material Substances 0.000 description 2
- -1 rare earth compound Chemical class 0.000 description 2
- 238000007493 shaping process Methods 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- 229910018137 Al-Zn Inorganic materials 0.000 description 1
- 229910018573 Al—Zn Inorganic materials 0.000 description 1
- 229910021323 Mg17Al12 Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 238000004581 coalescence Methods 0.000 description 1
- 238000004891 communication Methods 0.000 description 1
- 238000013016 damping Methods 0.000 description 1
- 230000003111 delayed effect Effects 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 230000005764 inhibitory process Effects 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 239000002667 nucleating agent Substances 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 238000005070 sampling Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
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Abstract
The heat treatment method of a kind of Mg-Al-Zn-Y magnesium-rare earth, carries out hot extrusion technique by magnesium-rare earth ingot casting, and extrusion temperature 340 DEG C ± 5 DEG C, extrusion ratio 5 ~ 7, after extruding, air cooling is to room temperature；Deformation material after extruding is carried out heat treatment: being first incubated 5 ~ 7h at 402 DEG C ~ 408 DEG C, air cooling is to room temperature；It is incubated 18 ~ 19h at 180 DEG C ~ 190 DEG C again, finally carries out air cooling；Described Mg-Al-Zn-Y magnesium-rare earth, each element accounts for total weight percent and is: Al is 8.3 ~ 9.7%, and Zn is 0.37 ~ 1.0%, and the percentage by weight of rare earth element y is 1.85% ~ 1.95%, and surplus is Mg.The present invention combines hot extrusion technique and heat treatment, the β-Mg after above-mentioned heat treatment, in As-extruded Mg-Al-Zn-Y magnesium-rare earth17Al12Hardening constituent all has Dispersed precipitate at intracrystalline and crystal boundary, and precipitated phase is the most tiny, the rare-earth phase Al of generation2Y presents corner passivation, and is mainly distributed on intracrystalline, so that mechanical property is obviously improved.
Description
Technical field
The invention belongs to Magnesium alloy AZ91D field.
Background technology
Magnesium alloy is little because having density, and specific strength is high, the advantage such as damping and amortization, machinability and good casting property, is typical lightweight metal material in actual applications, has good development space in automobile, communication and aerospace industry.But due to magnesium alloy shape that performance is poor, elastic modelling quantity is low, creep resistance and the shortcomings such as when intensity difference and solidification shrinkage factor is high during high temperature, the application of magnesium alloy can be caused again by limitation.
In recent years, rare earth element introduces magnesium alloy obtained paying close attention to widely to the performance improving magnesium alloy.Rare earth is a kind of excellent enhancing element to magnesium alloy, and concrete effect includes: cleaning molten effect, strengthens mobility effect, refined crystalline strengthening effect, solution strengthening effect and ageing strengthening effect.Major part rare earth element have be all close-packed hexagonal structure to Mg, atomic radius is close, lattice types is similar, a series of schedule of reinforcements such as causing distortion of lattice can be solid-solution in-Mg to improve the performances such as the intensity of magnesium-rare earth, hardness, make the range complete upgrading of magnesium-rare earth, the microstructure of magnesium-rare earth, crystal grain thinning can also be improved simultaneously；When Ageing Treatment, rare earth element hardening and strengthening effect are notable, and can form rare-earth phase first disperse educt, are greatly improved the mechanical property of magnesium-rare earth.Adding appropriate rare earth element to be because along with rare earth element content increases further, its ultimate tensile strength no longer improves, and declines on the contrary.This is the excess addition due to rare earth element, not only can make alloy structure coalescence, reduce the mechanical property of material, also can affect the normal use of magnesium-rare earth.
After pouring technology completes, magnesium-rare earth ingot casting, due to shrinkage factor height generation a large amount of casting flaws when it solidifies, may cause workpiece to be scrapped under serious conditions.In order to reduce casting flaw, hot extrusion technique can be used, will blank be heated to below recrystallization temperature after carry out extrusion process again.Hot extrusion pressure energy lifting workpieces compact rate of molding, the defect because of casting technique left over is greatly lowered, and to a certain degree reduce material grains size, deformation material is made to have certain stored energy, i.e. dislocation tangle produces stress concentration, meanwhile, equi-axed crystal can be formed and be uniformly distributed, thus the mechanical property of lifting workpieces.Selecting suitable extrusion temperature and extrusion ratio to have important impact to component shaping performance, extrusion temperature need to be less than alloy recrystallization temperature, but the too low meeting of extrusion temperature is because can not deforming and causing forming property difference to affect the effect of next step process completely；Extrusion ratio be according to the plastic deformation ability of alloy depending on, the too high meeting of extrusion ratio cause deform material remain a large amount of stress defects, cause workpiece to lose efficacy, extrusion ratio is too low can reduce component shaping performance.
Magnesium alloy is adding appropriate rare earth element y, then after hot extrusion technique, it is thus achieved that the mechanical property of As-extruded Mg-Al-Zn-Y magnesium-rare earth obtain and be obviously improved, but heterogeneous microstructure is insufficient to tiny and is evenly distributed.In order to improve heterogeneous microstructure fractions distribution, it can be carried out heat treatment, thus lifting workpieces mechanical property further.
Summary of the invention
Object of the present invention is to provide the heat treatment method of a kind of Mg-Al-Zn-Y magnesium-rare earth.Hot extrusion technique is combined by the inventive method with heat treatment phase, can significantly improve the mechanical property of alloy.
Mg-Al-Zn-Y magnesium-rare earth of the present invention, the most each element accounts for total weight percent and is: Al is 8.3 ~ 9.7%, and Zn is 0.37 ~ 1.0%, and the percentage by weight of rare earth element y is 1.85% ~ 1.95%, and surplus is Mg.
The heat treatment method of Mg-Al-Zn-Y magnesium-rare earth of the present invention.It is characterized in that: Mg-Al-Zn-Y magnesium-rare earth ingot casting carries out hot extrusion technique, and extrusion temperature 340 DEG C ± 5 DEG C, extrusion ratio 5 ~ 7, after extruding, air cooling is to room temperature；Deformation material after extruding is carried out heat treatment: being first incubated 5 ~ 7h at 402 DEG C ~ 408 DEG C, air cooling is to room temperature；It is incubated 18 ~ 19h at 180 DEG C ~ 190 DEG C again, finally carries out air cooling.Compared with tradition magnesium alloy, the solution have the advantages that:
Add appropriate rare earth element y in Mg-Al-Zn alloy, generate the Al of spherical shape2Y granule, this new rare-earth phase crystallization one step ahead alloy graining when, can conduct-Mg matrix and β-Mg17Al12The nucleating agent of phase, promote nucleus formation or be in crystallization front cause hinder dendrite tissue continue to grow up, finally reach the effect of Refining Mg Alloy tissue；This rare-earth phase separated out is high heat stability phase, improves elevated temperature strength and the creep resistance of alloy；Rare earth element y makes the dendrite β phase of continuous net-shaped distribution be gradually converted into the tiny equiaxed grain structure ruptured completely, improves the mechanical property of alloy.
In heat treatment process, after solution treatment, the β phase precipitation rate in-Mg supersaturated solid solution slows down, i.e. it is delayed alloy and reaches the time of aging peak, this is because the Al content during reaction generates rare-earth phase post consumption magnesium-rare earth in position, therefore have lost part β hardening constituent.Workpiece, after hot extrusion technique, can store a large amount of deformation energy, separates out the driving force providing sufficient for secondary phase, therefore compensate for the phenomenon of the delay of the aging peak caused because of the addition of rare earth element y.Rare Earth Y can make recrystallization temperature raise the recrystallization speed that slows down, and is effectively improved alloy microscopic structure, promotes material mechanical performance.
In the solution treatment stage, in tissue, form oversaturated-Mg solid solution the most completely, in the low temperature aging stage, can balance each other phase by secondary precipitation β in supersaturation-Mg solid solution.Contrast the cast magnesium alloy through fixation rates, its β phase amount of precipitation when Mg-Al-Zn-Y magnesium-rare earth reaches aging peak and not up to separates out completely, and the uneven components of precipitation strength phase, and grain boundaries exists pollution freemetallurgy, belong to discontinuous precipitation, be unfavorable for the mechanical property of alloy；And the β phase in Mg-Al-Zn-Y magnesium-rare earth shows as disconnected net distribution at grain boundaries, being then the point-like granule of small and dispersed distribution at intra-die, this has booster action for the organization mechanics performance of alloy.First the rare earth compound that Al with Y being solid-solution in-Mg matrix generates can separate out at intracrystalline or crystal boundary, heterogeneous nucleating center as matrix phase, promote magnesium-rare earth structure refinement, increase the quantity of nucleus, play refined crystalline strengthening effect, and rare-earth phase presents corner passivation, thus promote material mechanical performance.After heat treatment, accessible alloy the maximum tensile strength is 386.71MPa, and maximum elongation percentage is 12.8%, and highest hardness is 106.48HV.
Owing to secondary phase precipitation is evenly distributed on intracrystalline and grain boundaries by heat treatment, strengthen the inhibition of On Dislocation Motion, thus hinder instracrystalline slip and Grain Boundary Sliding, promote bearing capacity and the resistance of deformation of As-extruded Mg-Al-Zn-Y magnesium-rare earth, make alloy wear rate decrease, thus promote material wear ability.
Accompanying drawing explanation
Figure be described in the embodiment of the present invention 2 under conditions of the micro-organization chart of As-extruded Mg-Al-Zn-Y magnesium-rare earth.
Detailed description of the invention
The present invention will be described further by following embodiment, but the detailed description of the invention of the present invention is not limited to following embodiment.
Embodiment 1.
Mg-Al-Zn-Y magnesium-rare earth ingot casting is carried out hot extrusion, extrusion temperature 335 DEG C, extrusion ratio 5:1；At 402 DEG C, As-extruded Mg-Al-Zn-Y magnesium-rare earth is incubated 5h, and then air cooling is to room temperature；Again it is incubated 18h at 180 DEG C, finally carries out air cooling.After above-mentioned heat treatment, the tensile strength of As-extruded Mg-Al-Zn-Y magnesium-rare earth is 376.09MPa, and elongation percentage is 11.6%, and hardness is 98.86HV.
Embodiment 2.
Mg-Al-Zn-Y magnesium-rare earth ingot casting is carried out hot extrusion, extrusion temperature 340 DEG C, extrusion ratio 5:1；At 405 DEG C, As-extruded Mg-Al-Zn-Y magnesium-rare earth is incubated 6h, and then air cooling is to room temperature；Again it is incubated 19h at 190 DEG C, finally carries out air cooling.After above-mentioned heat treatment, the tensile strength of As-extruded Mg-Al-Zn-Y magnesium-rare earth is 386.67MPa, and elongation percentage is 12.8%, and hardness is 106.48HV.
Embodiment 3.
Mg-Al-Zn-Y magnesium-rare earth ingot casting is carried out hot extrusion, extrusion temperature 345 DEG C, extrusion ratio 6:1；At 408 DEG C, As-extruded Mg-Al-Zn-Y magnesium-rare earth is incubated 7h, and then air cooling is to room temperature；Again it is incubated 18h at 190 DEG C, finally carries out air cooling.After above-mentioned heat treatment, the tensile strength of As-extruded Mg-Al-Zn-Y magnesium-rare earth is 380.26MPa, and elongation percentage is 12.3%, and hardness is 102.39HV.
Workpiece sampling from embodiment 2, observes alloy microscopic structure, as shown in drawings after polishing, polish, corroding under an optical microscope.It can be seen in the drawings that after above-mentioned heat treatment, in alloy, form and the distribution of β phase are obviously improved, and all have Dispersed precipitate at intracrystalline and crystal boundary, and precipitated phase is the most tiny；The rare earth compound phase corner passivation generated, and it is mainly distributed on intracrystalline.
Claims (1)
1. a heat treatment method for Mg-Al-Zn-Y magnesium-rare earth, is characterized in that carrying out magnesium-rare earth ingot casting hot extrusion technique, and extrusion temperature 340 DEG C ± 5 DEG C, extrusion ratio 5 ~ 7, after extruding, air cooling is to room temperature；Deformation material after extruding is carried out heat treatment: being first incubated 5 ~ 7h at 402 DEG C ~ 408 DEG C, air cooling is to room temperature；Again at 180 DEG C ~ 190 DEG C
Insulation 18 ~ 19h, finally carries out air cooling；
Described Mg-Al-Zn-Y magnesium-rare earth, each element accounts for total weight percent and is: Al is 8.3 ~ 9.7%, and Zn is 0.37 ~ 1.0%, and the percentage by weight of rare earth element y is 1.85% ~ 1.95%, and surplus is Mg.
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| CN107523729A (en) * | 2016-06-20 | 2017-12-29 | 张家港市华舰五金工具有限公司 | Deformable rare earth magnesium alloy and preparation method thereof |
| CN107177762A (en) * | 2017-05-18 | 2017-09-19 | 湖南金戈新材料有限责任公司 | The secondary hot extrusion technique of AQ80M magnesium alloy profiles |
| CN109628813B (en) * | 2019-01-02 | 2021-05-28 | 中南大学 | Method for improving high-temperature creep resistance of rare earth magnesium alloy by using high-density precipitate-free zone |
| CN110607472A (en) * | 2019-10-30 | 2019-12-24 | 上海第二工业大学 | High-strength AZ81 magnesium alloy material containing Ce-based misch metal and preparation process thereof |
| CN115652158B (en) * | 2022-10-25 | 2023-08-11 | 西安交通大学 | Creep-resistant Mg-Al deformed magnesium alloy and preparation method thereof |
Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE10051525A1 (en) * | 2000-10-17 | 2002-05-02 | Thyssen Krupp Automotive Ag | Production of molded sheets made from forgeable magnesium-based alloys used as chassis parts in automobile construction comprises primary deforming, secondary deforming and preparing for a deep drawing process |
| CN1477221A (en) * | 2003-06-06 | 2004-02-25 | 中国第一汽车集团公司 | High-temp, creeping resistant compression casting magnesium alloy |
| JP2005281848A (en) * | 2004-03-02 | 2005-10-13 | Toyo Kohan Co Ltd | Magnesium thin sheet for flattening having excellent formability, and its production method |
| CN102644013A (en) * | 2012-05-07 | 2012-08-22 | 江汉大学 | High-strength and high-elongation cast magnesium alloy and production method thereof |
| CN103173703A (en) * | 2013-04-17 | 2013-06-26 | 重庆大学 | Process for improving age hardening effect of high-zinc deformed magnesium alloy |
| CN103397235A (en) * | 2013-08-16 | 2013-11-20 | 重庆大学 | Magnesium-aluminum-zinc-manganese-copper alloy and preparation method thereof |
| CN103436758A (en) * | 2013-08-05 | 2013-12-11 | 南昌大学 | Preparation method of magnesium-aluminum-zinc-yttrium magnesium alloy semisolid slurry |
| CN103774015A (en) * | 2014-01-18 | 2014-05-07 | 中南大学 | Forming process of medium-strong heat-resisting magnesium alloy triangular sectional material |
-
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- 2014-07-17 CN CN201410340276.4A patent/CN104152826B/en active Active
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE10051525A1 (en) * | 2000-10-17 | 2002-05-02 | Thyssen Krupp Automotive Ag | Production of molded sheets made from forgeable magnesium-based alloys used as chassis parts in automobile construction comprises primary deforming, secondary deforming and preparing for a deep drawing process |
| CN1477221A (en) * | 2003-06-06 | 2004-02-25 | 中国第一汽车集团公司 | High-temp, creeping resistant compression casting magnesium alloy |
| JP2005281848A (en) * | 2004-03-02 | 2005-10-13 | Toyo Kohan Co Ltd | Magnesium thin sheet for flattening having excellent formability, and its production method |
| CN102644013A (en) * | 2012-05-07 | 2012-08-22 | 江汉大学 | High-strength and high-elongation cast magnesium alloy and production method thereof |
| CN103173703A (en) * | 2013-04-17 | 2013-06-26 | 重庆大学 | Process for improving age hardening effect of high-zinc deformed magnesium alloy |
| CN103436758A (en) * | 2013-08-05 | 2013-12-11 | 南昌大学 | Preparation method of magnesium-aluminum-zinc-yttrium magnesium alloy semisolid slurry |
| CN103397235A (en) * | 2013-08-16 | 2013-11-20 | 重庆大学 | Magnesium-aluminum-zinc-manganese-copper alloy and preparation method thereof |
| CN103774015A (en) * | 2014-01-18 | 2014-05-07 | 中南大学 | Forming process of medium-strong heat-resisting magnesium alloy triangular sectional material |
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