CN104152826A - Heat treatment method for Mg-Al-Zn-Y rare-earth magnesium alloy - Google Patents
Heat treatment method for Mg-Al-Zn-Y rare-earth magnesium alloy Download PDFInfo
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- CN104152826A CN104152826A CN201410340276.4A CN201410340276A CN104152826A CN 104152826 A CN104152826 A CN 104152826A CN 201410340276 A CN201410340276 A CN 201410340276A CN 104152826 A CN104152826 A CN 104152826A
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- magnesium alloy
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- 229910052761 rare earth metal Inorganic materials 0.000 title claims abstract description 55
- 238000000034 method Methods 0.000 title claims abstract description 21
- 229910000861 Mg alloy Inorganic materials 0.000 title abstract description 15
- 150000002910 rare earth metals Chemical class 0.000 title abstract description 12
- 238000010438 heat treatment Methods 0.000 title abstract description 7
- 238000001125 extrusion Methods 0.000 claims abstract description 21
- 238000001816 cooling Methods 0.000 claims abstract description 15
- 238000001192 hot extrusion 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
- 238000005266 casting Methods 0.000 claims description 10
- 238000009413 insulation Methods 0.000 claims description 7
- 239000011777 magnesium Substances 0.000 abstract description 10
- 238000005728 strengthening Methods 0.000 abstract description 7
- 238000009826 distribution Methods 0.000 abstract description 3
- 238000002161 passivation Methods 0.000 abstract description 3
- 230000008569 process Effects 0.000 abstract description 3
- 229910021323 Mg17Al12 Inorganic materials 0.000 abstract 1
- 229910045601 alloy Inorganic materials 0.000 description 16
- 239000000956 alloy Substances 0.000 description 16
- 230000000694 effects Effects 0.000 description 11
- 230000032683 aging Effects 0.000 description 7
- 238000007669 thermal treatment Methods 0.000 description 6
- 239000013078 crystal Substances 0.000 description 5
- 238000001556 precipitation Methods 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 3
- 238000001953 recrystallisation Methods 0.000 description 3
- 239000000243 solution 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
- 238000005516 engineering process Methods 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 238000005498 polishing Methods 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
- 208000034189 Sclerosis Diseases 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000008859 change 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
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000013016 damping Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 230000006872 improvement 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
- 238000000879 optical micrograph Methods 0.000 description 1
- 230000008520 organization Effects 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
Abstract
The invention discloses a heat treatment method for an Mg-Al-Zn-Y rare-earth magnesium alloy. The method comprises the following steps: performing hot extrusion on a rare-earth magnesium alloy ingot, wherein the extrusion temperature is 340+/-5 DEG C, the extrusion ratio is 5-7, and performing air cooling to room temperature after extrusion; and performing heat treatment on the extruded deformation material, namely preserving the temperature to 402-408 DEG C for 5-7 hours, and performing air cooling to room temperature; and preserving the temperature to 180-190 DEG C, and finally performing air cooling. The Mg-Al-Zn-Y rare-earth magnesium alloy comprises the following elements in percentage by weight: 8.3-9.7 percent of Al, 0.37-1.0 percent of Zn, 1.85-1.95 percent of rare earth element Y and the balance of Mg. The hot extrusion process and heat treatment are combined; due to heat treatment, a beta-Mg17Al12 strengthening phase in the Mg-Al-Zn-Y rare-earth magnesium alloy in an extruded state has dispersed distribution in grains and grain boundary, the precipitated phase is uniform and fine, and the generated rare earth phase Al2Y is in corner passivation and is mainly distributed in grains, so that the mechanical property is obviously improved.
Description
Technical field
The invention belongs to magnesium alloy processing technique field.
Background technology
Magnesium alloy is little because having density, and specific tenacity is high, and the advantages such as damping and amortization, machinability and good casting property, are typical lightweight metal material in actual applications, have good development space in automobile, communication and space industry.But due to magnesium alloy shape that performance is poor, Young's modulus is low, intensity difference and the shortcoming such as shrinking percentage height while solidifying when creep resistance and high temperature, can cause again the application of magnesium alloy to be subject to limitation.
In recent years, rare earth element being introduced to the performance that magnesium alloy improves magnesium alloy has obtained paying close attention to widely.Rare earth is a kind of good enhancing element to magnesium alloy, and concrete effect comprises: cleaning molten effect, strengthens mobility effect, refined crystalline strengthening effect, solution strengthening effect and ageing strengthening effect.Most of rare earth element have to Mg be all close-packed hexagonal structure, atomic radius is close, lattice types is similar, can solid solution in ɑ-Mg, cause that a series of schedule of reinforcements such as lattice distortion improve the performance such as intensity, hardness of magnesium-rare earth, make the use range complete upgrading of magnesium-rare earth, can also improve the microtexture of magnesium-rare earth, crystal grain thinning simultaneously; In the time of ageing treatment, rare earth element sclerosis and strengthening effect are remarkable, and can form first disperse educt of rare-earth phase, have greatly promoted the mechanical property of magnesium-rare earth.Adding appropriate rare earth element is that its ultimate tensile strength no longer improves because along with ree content further increases, and declines on the contrary.This is because the excessive of rare earth element adds, and not only can make alloy structure coalescence, reduces the mechanical property of material, also can affect the normal use of magnesium-rare earth.
After pouring technology completes, when magnesium-rare earth ingot casting solidifies due to it, a large amount of casting flaw of the high generation of shrinking percentage, may cause workpiece to be scrapped in serious situation.In order to reduce casting flaw, can adopt hot extrusion technique, be heated to recrystallization temperature by blank and carry out again extrusion process after following.Hot extrude pressure energy lifting workpieces compact rate of molding, significantly reduce the defect of leaving over because of casting technique, and to a certain degree reduce material grains size, make to be out of shape material and there is certain stored energy, be that dislocation tangling produces stress concentration, meanwhile, can form equi-axed crystal and be uniformly distributed, thus the mechanical property of lifting workpieces.Select suitable extrusion temperature and extrusion ratio to have important impact to component shaping performance, extrusion temperature need be lower than alloy recrystallization temperature, but the too low meeting of extrusion temperature because can not be out of shape causes forming property poor and affect the effect of next step technique completely; Extrusion ratio be according to the plastic deformation ability of alloy and fixed, the too high meeting of extrusion ratio causes being out of shape the residual a large amount of stress defects of material, causes 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, and the mechanical property of the As-extruded Mg-Al-Zn-Y magnesium-rare earth of acquisition obtains obviously to be improved, but heterogeneous microstructure is enough not tiny and be evenly distributed.Distribute in order to improve heterogeneous microstructure form, can heat-treat it, thus further lifting workpieces mechanical property.
Summary of the invention
The object of the present invention is to provide a kind of heat treating method of Mg-Al-Zn-Y magnesium-rare earth.The inventive method is combined hot extrusion technique with heat treatment phase, can significantly improve the mechanical property of alloy.
Mg-Al-Zn-Y magnesium-rare earth of the present invention, wherein each element accounts for total weight percent and is: Al is that 8.3 ~ 9.7%, Zn is 0.37 ~ 1.0%, and the weight percent of rare earth element y is 1.85% ~ 1.95%, and surplus is Mg.
The heat treating 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 is carried out to hot extrusion technique, 340 DEG C ± 5 DEG C of extrusion temperatures, extrusion ratio 5 ~ 7, after extruding, air cooling is to room temperature; Distortion material after extruding is heat-treated: first, at 402 DEG C ~ 408 DEG C insulation 5 ~ 7h, air cooling is to room temperature; At 180 DEG C ~ 190 DEG C insulation 18 ~ 19h, finally carry out air cooling again.Compared with traditional magnesium alloy, technique effect of the present invention is:
Add appropriate rare earth element y in Mg-Al-Zn alloy, generate the Al of spherical shape
2y particle, this new rare-earth phase crystallization one step ahead in alloy graining, can serve as ɑ-Mg matrix and β-Mg
17al
12the nucleating agent of phase, promotes the formation of nucleus or causes hindering dentrite tissue in crystallization forward position to continue to grow up, and finally reaches the effect of Refining Mg Alloy tissue; This rare-earth phase of separating out is high heat stability phase, has improved hot strength and the creep resistance of alloy; Rare earth element y makes the dentrite β of continuous net-shaped distribution change gradually mutually the tiny equiaxed grain structure of fracture completely into, has promoted the mechanical property of alloy.
In heat treatment process, β phase precipitation rate after solution treatment in ɑ-Mg supersaturated solid solution slows down, postponed the time that alloy reaches aging peak, this is because the reaction Al content in magnesium-rare earth that generated rare-earth phase post consumption in position, therefore lost part β strengthening phase.Workpiece, after hot extrusion technique, can be stored a large amount of energy of deformation, separates out for secondary phase the motivating force that provides sufficient, has therefore made up the phenomenon of the delay of the aging peak causing because of adding of rare earth element y.Rare Earth Y can make the recrystallization temperature recrystallize speed that raises to slow down, and effectively improves alloy microscopic structure, promotes material mechanical performance.
In the solution treatment stage, be almost completed into oversaturated ɑ-Mg sosoloid in tissue, in the low temperature aging stage, phase can secondary precipitation β in supersaturation ɑ-Mg sosoloid balances each other.Contrast is through the cast magnesium alloys of solid solution aging processing, its β mutually amount of separating out does not reach completely and separates out in the time that Mg-Al-Zn-Y magnesium-rare earth reaches aging peak, and the uneven components of precipitation strength phase, and grain boundaries exists without separating out band, belong to discontinuous precipitation, be unfavorable for the mechanical property of alloy; And β in Mg-Al-Zn-Y magnesium-rare earth shows as disconnected net distribution at grain boundaries, be the point-like particle that small and dispersed distributes in crystal grain inside, this organization mechanics performance for alloy has booster action.First the Al of solid solution in ɑ-Mg matrix can separate out at intracrystalline or crystal boundary with the rare earth compound that Y generates, as the heterogeneous nucleating center of 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, thereby promote material mechanical performance.After thermal treatment, accessible alloy the maximum tensile strength is 386.71MPa, and maximum unit elongation is 12.8%, and highest hardness is 106.48HV.
Because thermal treatment is separated out secondary phase to be evenly distributed on intracrystalline and grain boundaries, strengthen the inhibition of On Dislocation Motion, thereby hinder instracrystalline slip and Grain Boundary Sliding, promote supporting capacity and the resistance to deformation of As-extruded Mg-Al-Zn-Y magnesium-rare earth, alloy wear rate is decreased, thereby promote material wear ability.
Brief description of the drawings
Figure is the micro-organization chart of As-extruded Mg-Al-Zn-Y magnesium-rare earth under the condition described in the embodiment of the present invention 2.
Embodiment
The present invention will be described further by following embodiment, but the specific embodiment of the present invention is not limited to following embodiment.
Embodiment 1.
Mg-Al-Zn-Y magnesium-rare earth ingot casting is carried out to hot extrusion, 335 DEG C of extrusion temperatures, extrusion ratio 5:1; By As-extruded Mg-Al-Zn-Y magnesium-rare earth, at 402 DEG C of insulation 5h, then air cooling is to room temperature; Again it is incubated to 18h at 180 DEG C, finally carries out air cooling.After above-mentioned thermal treatment, the tensile strength of As-extruded Mg-Al-Zn-Y magnesium-rare earth is 376.09MPa, and unit elongation is 11.6%, and hardness is 98.86HV.
Embodiment 2.
Mg-Al-Zn-Y magnesium-rare earth ingot casting is carried out to hot extrusion, 340 DEG C of extrusion temperatures, extrusion ratio 5:1; By As-extruded Mg-Al-Zn-Y magnesium-rare earth, at 405 DEG C of insulation 6h, then air cooling is to room temperature; Again it is incubated to 19h at 190 DEG C, finally carries out air cooling.After above-mentioned thermal treatment, the tensile strength of As-extruded Mg-Al-Zn-Y magnesium-rare earth is 386.67MPa, and unit elongation is 12.8%, and hardness is 106.48HV.
Embodiment 3.
Mg-Al-Zn-Y magnesium-rare earth ingot casting is carried out to hot extrusion, 345 DEG C of extrusion temperatures, extrusion ratio 6:1; By As-extruded Mg-Al-Zn-Y magnesium-rare earth, at 408 DEG C of insulation 7h, then air cooling is to room temperature; Again it is incubated to 18h at 190 DEG C, finally carries out air cooling.After above-mentioned thermal treatment, the tensile strength of As-extruded Mg-Al-Zn-Y magnesium-rare earth is 380.26MPa, and unit elongation is 12.3%, and hardness is 102.39HV.
The sampling of workpiece from embodiment 2, after polishing, polishing, corrosion at optical microphotograph Microscopic observation alloy microscopic structure, as shown in drawings.From accompanying drawing, can find out, after above-mentioned thermal treatment, in alloy, the form of β phase and the obviously improvement that distributes, all have disperse to distribute at intracrystalline and crystal boundary, and precipitated phase is more evenly tiny; The rare earth compound phase corner passivation generating, and be mainly distributed in intracrystalline.
Claims (1)
1. a heat treating method for Mg-Al-Zn-Y magnesium-rare earth, is characterized in that magnesium-rare earth ingot casting to carry out hot extrusion technique, 340 DEG C ± 5 DEG C of extrusion temperatures, and extrusion ratio 5 ~ 7, after extruding, air cooling is to room temperature; Distortion material after extruding is heat-treated: first, at 402 DEG C ~ 408 DEG C insulation 5 ~ 7h, air cooling is to room temperature; At 180 DEG C ~ 190 DEG C insulation 18 ~ 19h, finally carry out air cooling again;
Described Mg-Al-Zn-Y magnesium-rare earth, each element accounts for total weight percent and is: Al is that 8.3 ~ 9.7%, Zn is 0.37 ~ 1.0%, and the weight percent of rare earth element y is 1.85% ~ 1.95%, and surplus is Mg.
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| CN201410340276.4A CN104152826B (en) | 2014-07-17 | 2014-07-17 | A kind of heat treatment method of Mg-Al-Zn-Y magnesium-rare earth |
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| CN201410340276.4A CN104152826B (en) | 2014-07-17 | 2014-07-17 | A kind of heat treatment method of Mg-Al-Zn-Y magnesium-rare earth |
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| 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 |
| 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 |
| CN109628813A (en) * | 2019-01-02 | 2019-04-16 | 中南大学 | A method of improving magnesium-rare earth high temperature creep-resistant property using high density pollution freemetallurgy |
| 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 |
| CN115652158A (en) * | 2022-10-25 | 2023-01-31 | 西安交通大学 | Creep-resistant Mg-Al wrought magnesium alloy and preparation method thereof |
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| 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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| 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 |
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| 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 |
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| CN109628813A (en) * | 2019-01-02 | 2019-04-16 | 中南大学 | A method of improving magnesium-rare earth high temperature creep-resistant property using high density pollution freemetallurgy |
| 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 |
| CN115652158A (en) * | 2022-10-25 | 2023-01-31 | 西安交通大学 | Creep-resistant Mg-Al wrought magnesium alloy and preparation method 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 |
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| CN104152826B (en) | 2016-08-24 |
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