CN107557705A - A kind of preprocess method for improving wrought magnesium alloy mechanical property - Google Patents
A kind of preprocess method for improving wrought magnesium alloy mechanical property Download PDFInfo
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Abstract
The present invention is a kind of preprocess method for improving wrought magnesium alloy mechanical property.This method comprises the following steps：1）Homogenization Treatments and crimp；2）Pre-treatment：Above-mentioned bar is processed into tensile test bar, cupping machine is then placed on and carries out pre-treatment（Stretching or compression）, deflection is 0.5 ~ 20%；3）Subzero treatment；Magnesium alloy tensile test bar of the upper step after pre-treatment is positioned in liquid nitrogen environment, 0.5 ~ 24h of subzero treatment, takes out tensile test bar, be placed in air clear-cutting forestland to room temperature.The present invention can reach the purpose for improving magnesium alloy strength and toughness simultaneously, and strength and toughness is inverted relation after improving existing conventional annealing or T5, T6 aging strengthening model.
Description
Technical field
The present invention relates to a kind of heat treatment method for improving wrought magnesium alloy mechanical property, more particularly to one kind using deeply
Cold treatment improves the processing method of magnesium alloy strength and toughness.
Background technology
Magnesium alloy is that all structure metal and alloy materials Midst densities are minimum at present, has specific strength and specific stiffness
It is high, damping property is good, electromagnetic shielding and capability of resistance to radiation are strong, Cutting free processing, the easily series of advantages such as recovery, automobile, electronics,
The industrial circles such as electrical equipment, traffic, Aero-Space and national defence have extremely important application value and vast potential for future development.With
The increasingly depleted of the metallic mineral resources such as iron, aluminium, particularly in the environment of the energy, environmental protection problem become increasingly conspicuous, magnesium because
Aboundresources and be increasingly subject to pay attention to, be the 3rd metalloid structural material to grow up after steel and aluminium alloy, and by
Referred to as " 21 century green metal Structural Engineering material ".
Since the 1920s, with developing rapidly for material science, Principles of Heating Processing and technique have reached its maturity,
But conventional Technology for Heating Processing is difficult to greatly improve the intensity and toughness of metal simultaneously, in addition to refined crystalline strengthening, typically with sacrificial
The performance of domestic animal on the one hand exchanges the lifting of on the other hand performance for.In addition, the intensity of current material, toughness and wearability and paying no attention to
Think.So a kind of processing and treating method of magnesium alloy is urgently found, to improve the intensity and toughness of alloy simultaneously.
(the document 1 such as Z.R.Zeng：Z.R.Zeng et al.Annealing strengthening in a dilute
Mg–Zn–Ca sheet alloy.Scripta Materialia.2015,107:127-130.) research is found, at homogenization
Mg-0.3Zn-0.1Ca (at.%) magnesium alloy of reason, using pre-tension deformation technique, and after 200 DEG C of 1h that anneal, its tension is strong
Degree increases, but elongation percentage only slightly improves.And the process also needs to consumption compared with multiple-energy-source.In the prior art,
CN103233191A discloses a kind of Technology for Heating Processing for improving wrought magnesium alloy intensity, and the Technology for Heating Processing is in small deformation amount
Cold rolling after, then the artificial aging through different time, to reach the purpose for improving magnesium alloy strength.Meanwhile the Technology for Heating Processing
Economy and security it is poor, and simply improve the intensity of magnesium alloy, fail to improve alloy elongation percentage simultaneously.
To sum up, the shorter processing method of a kind of more economic, environmentally friendly, safety and process cycle is developed, while improves conjunction
Golden intensity and elongation percentage, Magnesium Alloys Components cost is reduced for final, improves Properties of Magnesium Alloy, and then realize it more wide
Application on wealthy field is significant.
The content of the invention
The present invention be directed to during existing magnesium alloy working process be difficult to improve its simultaneously using general Technology for Heating Processing it is strong
Degree and toughness, and complex process, the cycle is long, cost is too high, security is poor, so that it is difficult to mass industrialized production
The problems such as, there is provided it is a kind of for the economy of magnesium alloy, environmental protection, simplicity, security processing.The present invention passes through associated alloys element
Selection, to mainly containing high solid solubility element (Al, Sn, Zn etc.) or being easy to cyrystal boundary segregation element (RE, Ca, Zn etc.) deformed Mg
Alloy reaches the purpose for improving magnesium alloy strength and toughness using the technique of the compound subzero treatment of predeformation simultaneously, improves existing normal
Strength and toughness is inverted relation after rule annealing or T5, T6 aging strengthening model.
The technical scheme is that：
A kind of preprocess method for improving wrought magnesium alloy mechanical property, comprises the following steps：
1) Homogenization Treatments and crimp：Magnesium alloy is subjected to Homogenization Treatments, Homogenization Treatments under argon gas protection
Temperature is 350~500 DEG C, and the time is 6~24h, is subsequently placed in 35 DEG C of warm quenching-in water；It is again that the magnesium alloy after homogenization is pre-
Heat arrives 250-350 DEG C, with 0.08-0.12mm/s extrusion speed, 20:1 to 30:1 extrusion ratio, it is squeezed into a diameter of 8-12mm
Bar；
Described magnesium alloy is Mg-M, wherein, the one or more in M Gd, Li, Al, Sn, Bi, Ca, Zn and RE,
Its weight/mass percentage composition is the 0.5-15%, RE Y, Sc, Gd, Ce, Nd, Er or Ho of magnesium alloy；
2) pre-treatment：Above-mentioned bar is processed into tensile test bar, cupping machine is then placed on and is become in advance
Shape processing (stretching or compression), deflection is 0.5~20%；When reaching required deflection, stop stretching, then unload；
3) subzero treatment；By upper step after pre-treatment magnesium alloy tensile test bar leaching be placed in liquid nitrogen environment (-
196 DEG C), 0.5~24h of subzero treatment, tensile test bar is taken out, be placed in air clear-cutting forestland to room temperature；
This method also comprises the following steps：By step 1), 2), 3) after, then be repeated in step 2) and step 3) 2~
5 times, or individually repeat step 3) 2~5 times, wherein, repeat step 2) when, ensure total deformation≤20% of tensile test bar.
The present invention substantive distinguishing features be：
The present invention is reached by simple predeformation and subzero treatment combination process while improves the intensity of magnesium alloy and tough
Property purpose, improve strength and toughness after existing conventional annealing or T5, T6 aging strengthening model and be inverted relation.Predeformation can introduce greatly
Amount dislocation, twin, change Schmidt's factor and promote solid solution element to be segregated, while can be provided the defects of its generation for precipitated phase different
Matter forming core core substrate, promote forming core；Subzero treatment can promote the precipitation of Second Phase Particle by Lattice Contraction.With Conventional cryogenic
Annealing is different from aging technique, and subzero treatment (- 196 DEG C) can effectively avoid growing up, being roughened for crystal grain and the second phase, so as to avoid
The decline of intensity and plasticity.Present invention is generally directed to containing high solid solubility element (Al, Sn, Zn etc.) or easy cyrystal boundary segregation element
The wrought magnesium alloy system of (RE, Ca, Zn etc.) has excellent treatment effect, magnesium alloy can be made to obtain intensity in a short time
With the raising of toughness, so as to preferably meet industrial needs.
Beneficial effects of the present invention are：
1st, by simple predeformation and compound appropriate cryogenic treatment process, the defects of introducing a large amount of dislocations, twin, change and slide
Shifting is Schmidt's factor and causes solid solution element in fault location segregation, and follow-up subzero treatment Lattice Contraction disperse caused by low temperature is analysed
Go out a large amount of nanoscale Second Phase Particles, you can while the intensity and toughness of magnesium alloy are significantly improved, avoid Conventional cryogenic annealing
And aging strengthening model causes crystal grain and coarsening of second phase droplet to cause intensity and the inverted phenomenon of toughness.
2nd, liquid nitrogen used in subzero treatment is the byproduct of oxygen industry processed in the present invention, and cheap, raw material sources are wide, save
The energy, easy storage and transport, stable chemical performance, nontoxic pollution-free, compared with normative heat treatment, cost is extremely cheap.
3rd, equipment needed for the present invention is simple and convenient, and experimental period is short, simple to operate, safety, is advantageous to heavy industrialization
Using.
4th, the As-extruded Mg-10Gd that the As-extruded Mg-10Gd magnesium alloys after being handled using the inventive method are less processed
Magnesium alloy, yield strength improve 35.57%, and tensile strength improves 5.02%, and elongation percentage improves 81.58%.
5th, method of the invention is relative to (the document 1 such as Z.R.Zeng：Z.R.Zeng et al.Annealing
strengthening in a dilute Mg–Zn–Ca sheet alloy.Scripta Materialia.2015,107:
The method in research 127-130.), its yield strength and tensile strength are basically identical, but elongation percentage improves 89.04%.
Brief description of the drawings
Fig. 1 is the stress diagrams of the compound subzero treatment of Mg-10Gd magnesium alloy predeformation；
Fig. 2 is the stress diagrams of Mg-10Gd magnesium alloy predeformation compound cryosar annealing heat-treats.
Embodiment
Technical scheme is described further with embodiment below, following examples are in the present invention
Implemented under premised on technical scheme, give detailed embodiment and specific operating process, but the protection of the present invention
Scope is not limited to following embodiments.
Embodiment
Embodiment 1
From the ingot casting that composition is Mg-10Gd (wt.%), Homogenization Treatments are carried out to it, i.e., ingot casting are placed into box heat
In treatment furnace, 400 DEG C are warming up to stove, is incubated 12h, is subsequently placed in 35 DEG C of warm quenching-in water.Then by the casting after homogenization
Ingot is preheating to 250 DEG C, with 0.1mm/s extrusion speed, 25:1 extrusion ratio, it is squeezed into a diameter of 10mm bar.By bar
Tensile test bar is processed into, above-mentioned tensile test bar is then subjected to tensile pre-deformation processing, deflection 2% on cupping machine
(deflection is length), then unloads.Coupon is finally directly immersed in liquid nitrogen (- 196 DEG C) subzero treatment 1h, subzero treatment again
After end, tensile test bar is taken out, is placed in air clear-cutting forestland to room temperature.Stretching survey is carried out to the coupon after above-mentioned processing
Try (use GB/T 228.1-2010 metal material stretching test part 1 room temperatures test method), up to breaking, obtain stress-
Strain curve (as shown in Fig. 1 dashed curves, 202 ± 1MPa of yield strength, 251 ± 1MPa of tensile strength, elongation 27.6 ±
1.5%).
Embodiment 2
From the ingot casting that composition is Mg-10Gd (wt.%), Homogenization Treatments are carried out to it, i.e., ingot casting are placed into box heat
In treatment furnace, 400 DEG C are warming up to stove, is incubated 12h, is subsequently placed in 35 DEG C of warm quenching-in water.Then by the casting after homogenization
Ingot is preheating to 250 DEG C, with 0.1mm/s extrusion speed, 25:1 extrusion ratio, it is squeezed into a diameter of 10mm bar.By bar
Tensile test bar is processed into, above-mentioned tensile test bar is then subjected to tensile pre-deformation processing on cupping machine, deflection is
2%, then unload.Coupon is directly immersed in liquid nitrogen (- 196 DEG C) subzero treatment 1h, after subzero treatment terminates, takes out stretching examination
Rod, clear-cutting forestland is placed in air to room temperature.Repeat：Tensile test bar is carried out at tensile pre-deformation on cupping machine
Reason-deflection be 2%-immerse liquid nitrogen in (- 196 DEG C) subzero treatment 1h process twice.To the examination after above-mentioned processing
Rod carries out extension test (using GB/T 228.1-2010 metal material stretching test part 1 room temperatures test method), until drawing
It is disconnected, obtain 217 ± 2MPa of yield strength, 270 ± 2MPa of tensile strength, elongation 28.4 ± 1.5%.
Embodiment 3
From the ingot casting that composition is Mg-10Gd (wt.%), Homogenization Treatments are carried out to it, i.e., ingot casting are placed into box heat
In treatment furnace, 400 DEG C are warming up to stove, is incubated 12h, is subsequently placed in 35 DEG C of warm quenching-in water.Then by the casting after homogenization
Ingot is preheating to 250 DEG C, with 0.1mm/s extrusion speed, 25:1 extrusion ratio, it is squeezed into a diameter of 10mm bar.By bar
Tensile test bar is processed into, above-mentioned tensile test bar is then subjected to tensile pre-deformation processing on cupping machine, deflection is
2%, then unload.Coupon is directly immersed in liquid nitrogen (- 196 DEG C) subzero treatment 1h, after subzero treatment terminates, takes out stretching examination
Rod, clear-cutting forestland is placed in air to room temperature.Repeat (- 196 DEG C) subzero treatment 1h in coupon immersion liquid nitrogen twice.To warp
Cross the progress extension test of the coupon after above-mentioned processing and (use GB/T 228.1-2010 metal material stretching test part 1 room temperatures
Test method), until breaking, obtain 207 ± 2MPa of yield strength, 262 ± 2MPa of tensile strength, elongation 28.0 ± 1.5%.
Embodiment 4
For its step with embodiment 1, difference is that alloy is changed to Mg-6Bi (wt.%).234 ± 3Mpa of its yield strength,
244 ± 3Mpa of tensile strength, elongation 25.8 ± 1.4%.
Embodiment 5
For its step with embodiment 1, difference is that alloy is changed to Mg-3Al-1Zn (wt.%).Its yield strength 137 ±
3Mpa, 264 ± 3Mpa of tensile strength, elongation 22.3 ± 1.5%.
Embodiment 6
For its step with embodiment 1, difference is that alloy is changed to Mg-2Ca-5Zn (wt.%).Its yield strength 231 ±
2Mpa, 254 ± 2Mpa of tensile strength, elongation 14.2 ± 1.2%.
Embodiment 7
For its step with embodiment 1, difference is that alloy is changed to Mg-2Er (wt.%).172 ± 2Mpa of its yield strength,
212 ± 3Mpa of tensile strength, elongation 33.0 ± 1.5%.
Embodiment 8
For its step with embodiment 1, difference is that alloy is changed to Mg-4Sb (wt.%).180 ± 2Mpa of its yield strength,
212 ± 2Mpa of tensile strength, elongation 13.1 ± 1.5%.
Comparative example：
Comparative example 1
From the ingot casting that composition is Mg-10Gd (wt.%), Homogenization Treatments are carried out to it, i.e., ingot casting are placed into box heat
In treatment furnace, 400 DEG C are warming up to stove, is incubated 12h, is subsequently placed in 35 DEG C of warm quenching-in water.Ingot casting after homogenization is pre-
Heat is to 250 DEG C, with 0.1mm/s extrusion speed, 25:1 extrusion ratio, it is squeezed into a diameter of 10mm bar.Bar is processed
Into tensile test bar, extension test is carried out to the coupon after above-mentioned processing and (uses GB/T 228.1-2010 material during tensiles
Test part 1 room temperature test method), until breaking, obtain load-deformation curve and (shown in such as Fig. 1, Fig. 2 block curve, bend
Take 149 ± 1MPa of intensity, 239 ± 1MPa of tensile strength, elongation 15.2 ± 1.0%).
Comparative example 2
From the ingot casting that composition is Mg-10Gd (wt.%), Homogenization Treatments are carried out to it, i.e., ingot casting are placed into box heat
In treatment furnace, 400 DEG C are warming up to stove, is incubated 12h, is subsequently placed in 35 DEG C of warm quenching-in water.Ingot casting after homogenization is pre-
Heat is to 250 DEG C, with 0.1mm/s extrusion speed, 25:1 extrusion ratio, it is squeezed into a diameter of 10mm bar.Bar is processed
Into tensile test bar, coupon is directly immersed in liquid nitrogen (- 196 DEG C) subzero treatment 1h, after subzero treatment terminates, takes out stretching examination
Rod, clear-cutting forestland is placed in air to room temperature.Extension test is carried out to the coupon after above-mentioned processing and (uses GB/T228.1-
2010 metal material stretching test part 1 room temperature test methods), until breaking, obtain load-deformation curve (such as Fig. 1 dotted lines
Shown in curve, 164 ± 2MPa of yield strength, 246 ± 2MPa of tensile strength, elongation 22.9 ± 0.6%).
Comparative example 3
From the ingot casting that composition is Mg-10Gd (wt.%), Homogenization Treatments are carried out to it, i.e., ingot casting are placed into box heat
In treatment furnace, 400 DEG C are warming up to stove, is incubated 12h, is subsequently placed in 35 DEG C of warm quenching-in water.Ingot casting after homogenization is pre-
Heat is to 250 DEG C, with 0.1mm/s extrusion speed, 25:1 extrusion ratio, it is squeezed into a diameter of 10mm bar.Bar is processed
Into tensile test bar, then coupon is positioned in box heat treatment furnace and annealed, be warming up to 200 DEG C with stove, be incubated 1.5h, take
Go out tensile test bar, be placed in air clear-cutting forestland to room temperature.Extension test is carried out to the coupon after above-mentioned processing (to use
GB/T 228.1-2010 metal material stretching test part 1 room temperatures test method), until breaking, obtain stress-strain song
Line (as shown in Fig. 2 dot-dash curves, 175 ± 2MPa of yield strength, 255 ± 2MPa of tensile strength, elongation 16.4 ± 1.9%).
Comparative example 4
From the ingot casting that composition is Mg-10Gd (wt.%), Homogenization Treatments are carried out to it, i.e., ingot casting are placed into box heat
In treatment furnace, 400 DEG C are warming up to stove, is incubated 12h, is subsequently placed in 35 DEG C of warm quenching-in water.Ingot casting after homogenization is pre-
Heat is to 250 DEG C, with 0.1mm/s extrusion speed, 25:1 extrusion ratio, it is squeezed into a diameter of 10mm bar.Bar is processed
Into tensile test bar, above-mentioned tensile test bar is then subjected to tensile pre-deformation processing on cupping machine, deflection 2%, so
After unload.Coupon is positioned in box heat treatment furnace and annealed, 200 DEG C is warming up to stove, is incubated 1.5h, takes out stretching examination
Rod, clear-cutting forestland is placed in air to room temperature.Extension test is carried out to the coupon after above-mentioned processing and (uses GB/T228.1-
2010 metal material stretching test part 1 room temperature test methods), until breaking, obtain load-deformation curve (such as Fig. 2 dotted lines
Shown in curve, 207 ± 5MPa of yield strength, 259 ± 4MPa of tensile strength, elongation 14.6 ± 1.2%).
Comparative example 5
For its step with comparative example 1, difference is that alloy is changed to Mg-6Bi (wt.%).189 ± 3Mpa of its yield strength,
228 ± 3Mpa of tensile strength, elongation 19.1 ± 1.9%.
Comparative example 6
For its step with comparative example 1, difference is that alloy is changed to Mg-3Al-1Zn (wt.%).Its yield strength 116 ±
3Mpa, 244 ± 3Mpa of tensile strength, elongation 19.8 ± 1.4%.
Comparative example 7
For its step with comparative example 1, difference is that alloy is changed to Mg-2Ca-5Zn (wt.%).Its yield strength 220 ±
2Mpa, 240 ± 2Mpa of tensile strength, elongation 11.9 ± 1.2%.
Comparative example 8
For its step with comparative example 1, difference is that alloy is changed to Mg-2Er (wt.%).145 ± 2Mpa of its yield strength,
201 ± 3Mpa of tensile strength, elongation 28.0 ± 1.5%.
Comparative example 9
For its step with embodiment 1, difference is that alloy is changed to Mg-4Sb (wt.%).175 ± 2Mpa of its yield strength,
210 ± 2Mpa of tensile strength, elongation 15.2 ± 1.2%.
The embodiment data of table 1
The comparative example data of table 2
Table 1 illustrate heterogeneity As-extruded magnesium alloy sample it is processed by the invention after tensile mechanical properties.
Table 2 illustrates heterogeneity extruded Magnesium Alloy sample (AE)；As-extruded passes through the magnesium alloy sample of 1h liquid nitrogen deeps
(AE-DCT)；As-extruded passes through 1.5h, the magnesium alloy sample (AE-T5) of 200 DEG C of annealing；As-extruded is compound through 2% pre- modification
1.5h, the tensile mechanical properties of the magnesium alloy sample (AE-2%-T5) of 200 DEG C of annealing are as the contrast with embodiment.
Contrast table 1 and the data of table 2, composition are Mg-10Gd extruded Magnesium Alloy through a 2% pre- compound 1h of modification
Sample (AE-2%-DCT) after liquid nitrogen deep processing, 35.6% is improved compared with extruded Magnesium Alloy sample (AE) yield strength,
Tensile strength improves 5.0%, and elongation percentage improves 81.6%；Compared with magnesium alloy examination of the As-extruded after the processing of 1h liquid nitrogen deeps
Sample (AE-DCT) yield strength improves 23.1%, and tensile strength is basically identical, and elongation percentage improves 18.8%；Passed through compared with As-extruded
1.5h is crossed, magnesium alloy sample (AE-T5) yield strength of 200 DEG C of annealing improves 15.4%, and tensile strength is basically identical, extension
Rate improves 68.3%；Bent compared with As-extruded through the 2% pre- compound 1.5h of modification, the magnesium alloy sample (AE-2%-T5) of 200 DEG C of annealing
It is basically identical to take intensity, tensile strength is basically identical, and elongation percentage improves 86.3%.The As-extruded magnesium that composition is Mg-10Gd closes
Sample (AE- (2%-DCT) * 3) of the gold after 2% predeformation and 1h liquid nitrogen deeps handle two steps in triplicate is compared with As-extruded
Sample (AE-2%-DCT) yield strength of magnesium alloy after a 2% pre- compound 1h liquid nitrogen deeps processing of modification improves
7.4%, tensile strength improves 7.5%, and elongation percentage improves 2.9%.Composition is Mg-10Gd extruded Magnesium Alloy through once
Sample (AE-2%- (DCT) * 3) after the compound liquid nitrogen deeps of the 1h three times processing of 2% predeformation is compared with extruded Magnesium Alloy through once
Sample (AE-2%-DCT) yield strength after the 2% pre- compound 1h liquid nitrogen deeps processing of modification improves 2.5%, and tensile strength carries
High by 4.4%, elongation percentage improves 1.4%.Composition is Mg-6Bi extruded Magnesium Alloy through a 2% pre- modification and a 1h
Sample (AE-2%-DCT) after liquid nitrogen deep processing improves 23.8% compared with extruded Magnesium Alloy sample (AE) yield strength, resists
Tensile strength improves 7.0%, and elongation percentage improves 35.1%.Composition is Mg-3Al-1Zn extruded Magnesium Alloy through one time 2%
Sample (AE-2%-DCT) after pre- modification and a 1h liquid nitrogen deeps processing is compared with extruded Magnesium Alloy sample (AE) yield strength
18.1% is improved, tensile strength improves 8.2%, and elongation percentage improves 12.6%.Composition is Mg-2Ca-5Zn As-extruded
Sample (AE-2%-DCT) of the magnesium alloy after a 2% pre- modification and a 1h liquid nitrogen deeps processing tries compared with extruded Magnesium Alloy
Sample (AE) yield strength improves 5%, and tensile strength improves 5.8%, and elongation percentage improves 19.3%.Composition is Mg-2Er's
Sample (AE-2%-DCT) of the extruded Magnesium Alloy after a 2% pre- modification and a 1h liquid nitrogen deeps processing is compared with As-extruded magnesium
Alloy sample (AE) yield strength improves 18.6%, and tensile strength improves 5.4%, and elongation percentage improves 17.9%.Form
It is divided into sample (AE-2%-DCT) of the Mg-4Sb magnesium alloy after a 2% pre- modification and a 1h liquid nitrogen deeps processing relatively to squeeze
Pressure state magnesium alloy sample (AE) yield strength only enhances 2.8%, and tensile strength does not change, and elongation percentage reduces on the contrary
13.8%, further illustrate this patent practical alloy be only limited to containing high solid solubility element (Al, Sn, Zn etc.) or easily crystal boundary it is inclined
Analyse the wrought magnesium alloy system of element (RE, Ca, Zn etc.).
In summary, for the magnesium alloy materials with ageing strengthening feature, at the suitable compound deep cooling of predeformation
Reason overcomes the shortcomings that conventional predeformation adds annealing/aging strengthening model, is separated out and suppressed by nano-second-phase under low temperature environment
Crystal boundary migration realizes the synchronous raising of intensity and toughness.
The above embodiment of the present invention is only example to illustrate the invention, and is not the implementation to the present invention
The restriction of mode.For those of ordinary skill in the field, other can also be made not on the basis of the above description
With the change and variation of form.Here all embodiments can not be exhaustive.It is every to belong to technical scheme
Row of the obvious changes or variations amplified out still in protection scope of the present invention.
Unaccomplished matter of the present invention is known technology.
Claims (2)
- A kind of 1. preprocess method for improving wrought magnesium alloy mechanical property, it is characterized in that this method comprises the following steps：1）Homogenization Treatments and crimp：Magnesium alloy is subjected to Homogenization Treatments, Homogenization Treatments temperature under argon gas protection For 350 ~ 500 DEG C, the time is 6 ~ 24h, is subsequently placed in 35 DEG C of warm quenching-in water；The magnesium alloy after homogenization is preheating to again 250-350 DEG C, with 0.08-0.12mm/s extrusion speed, 20:1 to 30:1 extrusion ratio, it is squeezed into a diameter of 8-12mm rod Material；Described magnesium alloy is Mg-M, wherein, the one or more in M Gd, Li, Al, Sn, Bi, Ca, Zn and RE, its matter Measure the 0.5-15%, RE Y, Sc, Gd, Ce, Nd, Er or Ho that percentage composition is magnesium alloy；2）Pre-treatment：Above-mentioned bar is processed into tensile test bar, cupping machine is then placed on and carries out at predeformation Reason（Stretching or compression）, deflection is 0.5 ~ 20%；When reaching required deflection, stop stretching, then unload；3）Subzero treatment；Magnesium alloy tensile test bar of the upper step after pre-treatment is positioned in liquid nitrogen environment（-196 ℃）, 0.5 ~ 24h of subzero treatment, tensile test bar is taken out, is placed in air clear-cutting forestland to room temperature.
- 2. the preprocess method of wrought magnesium alloy mechanical property is improved as claimed in claim 1, it is characterized in that also including as follows Step：Passing through step 1）、2）、3）Afterwards, then it is repeated in step 2）- step 3）2 ~ 5 times, or individually repeat step 3）2~5 It is secondary, wherein, repeat step 2）When, ensure total deformation≤20% of tensile test bar.
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| CN109837437A (en) * | 2019-02-27 | 2019-06-04 | 吉林大学 | A kind of alternating temperature controlled rolling preparation method for making low content magnesium alloy that there is uniform fine grain |
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| CN107557705B (en) | 2018-12-28 |
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