CN106801206A - A kind of method of the Mg RE Zn systems Alloy At Room Temperature plasticity for improving the phase of structure containing LPSO - Google Patents
A kind of method of the Mg RE Zn systems Alloy At Room Temperature plasticity for improving the phase of structure containing LPSO Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/06—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of magnesium or alloys based thereon
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
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Abstract
The invention discloses a kind of method of the Mg RE Zn systems Alloy At Room Temperature plasticity for improving the phase of structure containing LPSO, belong to metal heat treatmet and phase transformation field.The method just as cast condition Mg RE Zn system's alloys carry out two-step homogenization heat treatment under conditions of 480 ± 10 DEG C × 24h+500 ± 5 DEG C × 32h, subsequent alloy is incubated 2h ± 10min at cooling to 460~480 DEG C with the furnace, obtains the Mg RE Zn systems alloy of the structure phases of LPSO containing needle-like.Mg RE Zn systems alloy is prepared using the inventive method, in the case where material mechanical performance change amplitude is little, material elongation after fracture is significantly improved, i.e., temperature-room type plasticity is significantly improved.
Description
Technical field
The invention belongs to metal material heat treatment and phase transformation field, and in particular to one kind improves the phase of ordered structure containing long period
The method of the Mg-RE-Zn Alloy At Room Temperature plasticity of (abbreviation LPSO structures phase).
Background technology
Mg-RE systems alloy because with excellent room temperature and mechanical behavior under high temperature, high-temerature creep drag higher and good
Corrosion resistance, thus the research and application of Mg-RE systems alloy are more and more extensive.
Recently, scientific research discovery, Mg-RE-TM (TM=Zn, Cu, Ni, Co；RE=Y, Gd, Dy, Ho, Er, Tm, Tb) and
There is a kind of long period orderly stacking (LPSO) structure phase in Mg-Al-Gd alloys, LPSO structures are both mutually a kind of long-periodic structure
Ordered phase and be also a kind of chemically-ordered phase, the Mg-RE-Zn alloys containing LPSO structure phases have combination property higher,
At present, this kind of alloy has become one of focus of magnesium alloy research.
Magnesium alloy will generally carry out homogenization heat treatment before pressure processing, and main purpose is to eliminate eutectic structure on crystal boundary
In thick eutectic structure in β phases because this phase belongs to brittlement phase, strain cracking can be caused in hot procedure.Contain
After the Mg-RE-Zn systems alloy homogenization heat treatment of LPSO structure phases, can be at original grain boundary after the β phase back dissolvings in eutectic structure
Bulk LPSO structure phases are produced, the presence of this block LPSO structures phase can not to greatest extent improve Mg-RE-Zn systems alloy
Plasticity.
It is with Mg-7Gd-3Y-1Nd-1Zn-0.5Zr alloys as object, Mg-7Gd-3Y-1Nd-1Zn-0.5Zr alloys is uniform
After changing heat treatment, can occur the 14H type LPSO structure phases of bulk morphologies on crystal boundary, as shown in Figure 1.Along<11-20>α directions
Tem analysis understand：The atom way of stacking of 14H-LPSO structure phases is ABABABACBCBCBC, as shown in Fig. 2 this stacking
Mode can regard as and be composited by close-packed hexagonal structure unit ABABAB, CBCBCBC and face-centred cubic structure unit ABC,
So as to the atom way of stacking of the Mg-RE-Zn systems alloy of the phase of structure containing LPSO can be regarded as by close-packed hexagonal structure
Atom way of stacking ... the ABC ... of atom way of stacking ... AB ... and face-centred cubic structure is composited.Can according to dislocatioln theory
Know：In plastic history, basal slip system is main deformation mechanism in the Mg crystal of close-packed hexagonal structure, in face-centered cubic
The crystal Dislocations of structure can not only slide, and be easy to carry out commutative Banach aglebra, and this is the Mg-RE- containing LPSO structure phases
Zn systems alloy has one of major reason of high-ductility.
Based on above-mentioned analysis, it is believed that the microstructure of the high-ductility Mg-RE-Zn systems alloy of the phase of structure containing LPSO should have
Have at following 2 points：(1) face-centred cubic structure unit proportion is high, and this requires the volume fraction of LPSO structure phases as far as possible
It is high.Common practice is exactly the type for increasing Zn contents or changing LPSO structure phases.Although increasing Zn contents can make LPSO
The volume fraction of structure phase is raised, but the consumption of RE elements is increased simultaneously, is further dropped low-alloyed precipitation strength and is imitated
Really.It periodicity LPSO structural phase transitions long is periodically short LPSO structure phases that the type for changing phase is exactly, such as 24R or
Person 18R changes into 14H or 10H, but phase in version thermodynamic condition and dynamic conditions not malleable, phase in version is difficult reality
It is existing；(2) face-centred cubic structure unit should be distributed in α-Mg matrixes, and this is accomplished by changing the distribution of LPSO structure phases.
The pattern of LPSO structure phases can be divided into the block and transgranular needle-like of crystal boundary, and the presence of crystal boundary bulk LPSO structure phases makes
Face-centered cubic unit is excessively assembled, and the presence of transgranular needle-like LPSO structure phases makes face-centred cubic structure unit more dispersed, because
And needle-like LPSO structures should mutually improve the effect is significant of alloy plasticity relative to the raising effect of plasticity than block LPSO structures.
It is existing be related to regulation and control magnesium alloy in long period ordered structure phase method be mainly in process of setting by ultrasound shake
Move to change the pattern of bulk LPSO phases on crystal boundary, such as patent of Application No. 201610846456.9, this effect is very
It is limited, and be not directed to how to make the block LPSO structures existed in microstructure after solidification mutually how to be transformed into needle-like LPSO to tie
Structure phase, and then improve alloy plasticity.
The content of the invention
In view of the deficiencies in the prior art, it is an object of the invention to provide a kind of Mg-RE-Zn for improving the phase of structure containing LPSO
It is the method for Alloy At Room Temperature plasticity, bulk LPSO structures phase in version in magnesium alloy after heat treatment can be needle-like LPSO by the method
Structure phase, and then improve alloy plasticity.
The invention provides a kind of method of the Mg-RE-Zn systems Alloy At Room Temperature plasticity for improving the phase of structure containing LPSO, by as cast condition
Mg-RE-Zn systems alloy carries out two-step homogenization heat treatment under conditions of 480 ± 10 DEG C × 24h+500 ± 5 DEG C × 32h, then
Alloy is incubated 2h ± 10min at cooling to 460~480 DEG C with the furnace, obtains the Mg-RE-Zn systems alloy of the structure phases of LPSO containing needle-like.
Preferably, the two-step homogenization heat treatment condition is 480 DEG C × 24h+500 DEG C × 32h.
Further, the temperature of the alloy furnace cooling is 480 DEG C.
Further, soaking time is 2h after alloy furnace cooling.
Hot extrusion step is additionally provided with after furnace cooling incubation step, quenching cooling, institute immediately after the completion of hot extrusion step
To state before hot extrusion step is specially extruding, by blank heating to 500 DEG C, be incubated 2~3h, during extruding, extruding rate is 0.2~
2mm/s, extrusion ratio is 16:1.
Aging strengthening model is provided with after quenching cooling, aging strengthening model temperature is 200~225 DEG C, the time is 30h.
Preferably, the aging strengthening model temperature is 200 DEG C.
Preferably, the as cast condition Mg-RE-Zn systems alloy is Mg-7Gd-3Y-1Nd-1Zn-0.5Zr alloys.
Further, the as cast condition Mg-RE-Zn systems alloy Mg-Gd-Y-Zn-Zr alloys.
The present invention has the following technical effect that relative to prior art：
The inventive method only by after two-step homogenization is heat-treated increase furnace cooling step, and limiting temperature and when
Between, you can by the block LPSO structural phase transitions on alloy crystal boundary into the needle-like LPSO structure phases in α-Mg matrixes, in tensile strength
And in the case of Proof strength of non-proportional change less, its elongation after fracture is significantly improved, and the inventive method is simple,
It is not required to improve alloy plasticity by increasing other auxiliary equipments, is capable of achieving industrialized production.
Brief description of the drawings
Fig. 1 is the Mg-7Gd-3Y-1Nd-1Zn-0.5Zr alloys of the phase of structure containing 14H-LPSO after two-step homogenization heat treatment
Metallograph；
Fig. 2 is 14H-LPSO structure phase high resolution graphics；
After Fig. 3 is heat-treated 24h at different temperatures for as cast condition Mg-7Gd-3Y-1Nd-1Zn-0.5Zr (wt.%) alloy
Microstructure evolution figure, (a) heat treatment temperature is 420 DEG C in figure, and (b) heat treatment temperature is 440 DEG C, and (c) heat treatment temperature is
460 DEG C, (d) heat treatment temperature is 480 DEG C, and (e) heat treatment temperature is 500 DEG C；
Fig. 4 is that as cast condition Mg-7Gd-3Y-1Nd-1Zn-0.5Zr (wt.%) alloys different time at 480 DEG C is heat treated
Microstructure evolution figure in journey, (a) is 0.5h in figure, and (b) is 2h, and (c) is 4h, and (d) is 16h, and (e) is 48h；
Fig. 5 is to be cooled to difference with stove after as cast condition Mg-7Gd-3Y-1Nd-1Zn-0.5Zr (wt.%) two-step homogenization is heat-treated
The Morphology figure of 14H type LPSO structure phases after temperature and at such a temperature insulation different time, a is under 480 DEG C × 2h in figure
Insulation, b is insulation under 480 DEG C × 4h, and c is insulation under 480 DEG C × 6h, and d is insulation under 460 DEG C × 2h, and e is under 460 DEG C × 4h
Insulation, f is insulation under 460 DEG C × 6h, and g is insulation under 440 DEG C × 2h, and h is insulation under 440 DEG C × 6h, and i is under 440 DEG C × 6h
Insulation；
Fig. 6 is tissue topography's figure of alloy after different disposal, and a is the group after two-step homogenization+furnace cooling+extruding in figure
Knit, b be two-step homogenization heat treatment after+extruding after tissue；
Fig. 7 is the age hardening curves after alloy peak timeliness heat treatment under different temperatures；
Fig. 8 is metallograph after peak timeliness heat treatment, and a is selection electron diffraction spot, crystal zone axis // [0001] α side in figure
To b is bright field image, and c is low power HAADF-STEM X rays topographs, and d is high power HAADF-STEM X rays topographs；
Fig. 9 is the mechanical property comparison diagram of alloy A and B, and alloy A is that directly extruding is obtained after two-step homogenization is heat-treated
Alloy, alloy B be two-step homogenization heat treatment after furnace cooling extrude again after alloy, in figure a be ultimate tensile strength
(UTS), yield strength (YS), elongation percentage (Elongation) comparison diagram, figure b are the load-deformation curve of alloy A, and figure c is conjunction
The load-deformation curve of golden B, 3 parallel samples are cut when 1,2,3 is test mechanical property in figure；
Figure 10 is the mechanical property comparison diagram of alloy A and B after peak timeliness heat treatment, and a is ultimate tensile strength in figure
(UTS), yield strength (YS), elongation percentage (Elongation) comparison diagram, figure b are the load-deformation curve of alloy A, and figure c is conjunction
The load-deformation curve of golden B, 1,2,3 implications are consistent with Fig. 9 in figure.
Specific embodiment
Specific embodiment of the invention is described further below in conjunction with the accompanying drawings.
Embodiment 1
Specific embodiment of the invention comprises the following steps：
1st, alloy melting
It is that 100 × 400mm of Φ calculate dispensing according to die size, raw material is pure Mg blocks, pure rare earth Gd, Y and Nd, pure Zn blocks
With Mg-30wt.%Zr intermediate alloys.It is 5kg that ingot casting weight is designed before melting, and being calculated by the result of melting and composition test can
：Mg recovery rates are 98.8%, and the recovery rate of pure RE is that 90%, Zn recovery rates are 100%, Mg-30wt.%Zr intermediate alloys
Recovery rate is 25%.
Preparation before 1.1 meltings
(1) weigh, prepare furnace charge, first by the erosion on furnace charge, oxide removal, toolrust-removal, all moulds, original
Material, flux etc. are preheating to 150 DEG C；
(2) protective gas pipeline is connected, protective gas selects Ar2Gas, with steel crucibles melting magnesium alloy, in fusion process
In protect always, temperature control is the important step of magnesium alloy smelting process.When temperature is relatively low, oxidation rate is little, higher than 500
DEG C when, oxidation rate accelerate, during more than 750 DEG C, oxidation rate is sharply increased, and higher than 1120 DEG C, Serum Magnesium largely gasifies, and causes
Blast.In fusion process, thermocouple is put into, monitors smelting temperature.
1.2 alloy meltings
(1) magnesium ingot is added into crucible, appropriate flux is sprinkled in sidewall of crucible and bottom, heat up fusing under low-power；
(2) alloying：When Mg liquid temperature degree reaches 750 DEG C, pure rare earth Gd, Y and Nd, pure Zn blocks are sequentially added after skimming；
When melt temperature rises to 850 DEG C, Mg-30wt.%Zr intermediate alloys are added, all after fusing, stir 2~5min, make alloy
Elemental redistribution is homogenized；
(3) refine：First, magnesium alloy solution temperature, 750~760 DEG C are adjusted；Secondly, upper and lower 4~8min of vertical stirring,
Continuous uniform sprinkles refining flux in whipping process；Again, the flux on sidewall of crucible and aluminium alloy surface is removed, then spreads one layer and covered
Lid flux.10~20min is stood after refining, makes field trash sedimentation separation.
(4) pour into a mould：First skimmed before cast, be down to 700 DEG C of pouring temperature and poured into a mould.
2nd, homogenization heat treatment
In order to eliminate or reducing microsegregation, improve the processing characteristics of alloy, alloy cast ingot must be carried out before being deformed
Homogenize heat treatment (i.e. homogenizing annealing).It is general using two-step homogenization heat in order to ensure good homogenization thermal effectiveness
Treatment, two-step homogenization heat treatment condition is 480 DEG C × 24h+500 DEG C × 32h.
3rd, the regulation and control of bulk 14H type LPSO structures phase morphology and hot extrusion
The oxide skin of blank surface after two-step homogenization is removed with lathe, the blank of 90 × 200mm of Φ is processed into, with stove
480 DEG C of cooling, and 2 hours are incubated at 480 DEG C, the step can make the block 14H types LPSO structure phase in version Cheng Jing on crystal boundary
The needle-like 14H type LPSO structure phases in intragranular portion.
4th, hot extrusion
Before extruding, mould and blank are placed in Muffle furnace with stove heat to 500 DEG C, and are incubated 2~3h, recipient temperature
400 DEG C, extrusion speed is controlled in the range of 0.2~2mm/s, and the diameter of rod after extruding is 20mm, and extrusion ratio is 16：1, extruding
After the completion of immediately with Water spray quench cool down, it is therefore an objective to avoid excessive deformation precipitated phase from producing.In tissue such as Fig. 6 after extrusion
Shown in a, in order to be contrasted, b is the tissue after directly being extruded after homogenization is heat-treated in Fig. 6.
5th, peak timeliness heat treatment
Aging strengthening model is carried out in blast furnace, peak timeliness heat treatment temperature is respectively 200 DEG C, 225 DEG C and 250 DEG C.When
Effect hardening curve is as shown in fig. 7, it is 200 DEG C × 30h, peak to select optimal peak timeliness heat treating regime according to age hardening curves
Precipitated phase after timeliness is β ' phases, as shown in Figure 8.
6th, interpretation
Alloy extrusion state, the room-temperature mechanical property difference of extruding+peak timeliness heat treatment state are as shown in Figures 9 and 10.In order to just
In mark, directly the alloy of extruding is designated as alloy A (Alloy A), two-step homogenization heat treatment after two-step homogenization is heat-treated
Alloy B (Alloy B) is designated as with alloy of the stove stove after cold.Be can be seen that from Fig. 9 and 10：Needle-like 14H types LPSO structures in alloy
The presence of phase is obviously improved the elongation percentage of alloy.
The present invention is had found by above-mentioned experiment：Cast alloy, with the rising of heat treatment temperature, has in heat treatment process
Beneficial to the formation bulk 14H type LPSO structure phases on crystal boundary；With the reduction of heat treatment temperature, be conducive to being formed in intra-die
Needle-like 14H type LPSO structure phases, as shown in Figure 3.When the timing of heat treatment temperature one finds：The heat treatment initial stage is conducive to needle-like 14H
The formation of type LPSO structure phases, with the extension of heat treatment time, needle-like 14H type LPSO structures mutually fade away, finally in crystalline substance
Bulk 14H type LPSO structure phases are formed in boundary, as shown in Figure 4.Therefore heat treatment is will be seen that and solved by the inventive method
During 14H type LPSO structure phases Morphology rule.
Secondly, the present invention is obtained according to 14H types LPSO structure phase morphology development laws in heat treatment process：Low-temperature short-time heat
Treatment can be conducive to producing needle-like 14H type LPSO structure phases in α-Mg matrixes, and main cause is lower temperature, RE elements α-
The solid solubility of Mg matrixes is smaller, while be conducive to Zn atoms to be spread in α-Mg matrixes under low temperature, the final shape in α-Mg matrixes
Into needle-like 14H type LPSO structure phases.According to this thought, the present invention preferably, by cast alloy by 480 DEG C × 24h+500
DEG C × heat treatment of 32h two-step homogenizations, the β phases in eutectic structure are eliminated, while making to produce bulk 14H type LPSO structures on crystal boundary
Phase；Then the alloy after two-step homogenization is heat-treated finds after being cooled to different temperatures and at such a temperature insulation 2h with stove：With
Stove is cooled to different temperatures and needle-like 14H type LPSO structure phases is occurred in that in α-Mg matrixes, as shown in figure 5, and needle-like 14H types
LPSO structures increase with the reduction of heat treatment temperature or the extension of time, and the block 14H types LPSO knots on crystal boundary
Structure phase then constantly diminishes with the reduction or the extension of time its size of heat treatment temperature, illustrates bulk 14H type LPSO structures
Decomposing phenomenon is occurred in that during furnace cooling.Black particle on crystal boundary mutually belongs to Mg-RE phase particles, and this phase belongs to
Brittlement phase, can cause cracking in thermal deformation process when size is larger, while heavy during reducing follow-up aging strengthening model
Form sediment and strengthen effect, therefore black particle is not intended to appearance during tissue modulation.Consider, optimal furnace cooling system
Degree selection is 480 DEG C × 2h.Above-mentioned treatment can be heat-treated homogenization after block 14H types LPSO structural phase transitions on crystal boundary into
Needle-like 14H type LPSO structure phases in α-Mg matrixes.
Embodiment 2
Morphological control based on LPSO structure phases proposed by the present invention and the method that improves Alloy At Room Temperature plasticity is by as cast condition
Mg-RE-Zn systems alloy is by obtaining block LPSO structures phase, alloy after two-step homogenization heat treatment after two-step homogenization heat treatment
After cool to a certain temperature with the furnace and carry out isothermal treatment for short time, and can not occur Mg-RE in microstructure during furnace cooling
Phase particle and precipitated phase, so as to be needle-like LPSO structure phases by block LPSO structures phase in version.Then, carry out follow-up hot extrusion and
Aging strengthening model, finally obtains the Mg-RE-Zn systems alloy of the structure phases of LPSO containing needle-like of high-ductility.
The method is applied to the Mg-RE-Zn systems alloy of all phases of structure containing LPSO, and simply specific technological parameter is according to alloy
The difference of composition and make corresponding adjustment.And the adjustment be those of ordinary skill in the art according to method disclosed by the invention and
Existing known technology can be derived naturally, therefore the present invention carries out contrast to different Mg-Gd-Y-Zn systems alloy in fact
Test, respectively as shown in Tables 1 and 2, wherein table 1 is As-extruded Mg-Gd-Y-Zn systems alloy to the material mechanical performance test result for obtaining
Mechanical property (only containing block LPSO structures phase) after extruding+peak timeliness, table 2 be As-extruded Mg-Gd-Y-Zn systems alloy extrusion+
Mechanical property (structures of LPSO containing needle-like phase) after peak timeliness, i.e. process of the test as described in Example 1, except that in table 2
Alloy has furnace cooling and incubation step, and then without the step in table 1.
Table 1
| Alloy | Rm(MPa) | Rp0.2(MPa) | A (%) |
| Mg-5Gd-4Y-0.5Zn-0.4Zr | 370 | 300 | 6.0 |
| Mg-6Gd-3Y-1Zn-0.5Zr | 328 | 260 | 9.3 |
| Mg-6Gd-3Y-1.4Zn-0.5Zr | 425 | 369 | 6 |
| Mg-6Gd-3Y-1.5Zn-0.5Zr | 372 | 310 | 7.7 |
| Mg-6Gd-3Y-2Zn-0.5Zr | 403 | 336 | 7.0 |
| Mg-7Gd-4Y-0.5Zn-0.5Zr | 392.5 | 327.1 | 8.5 |
| Mg-7Gd-4Y-1.5Zn-0.5Zr | 446 | 399 | 6.1 |
| Mg-7Gd-4Y-2.5Zn-0.5Zr | 457 | 414 | 4.6 |
| Mg-8.2Gd-3.8Y-1Zn-0.3Zr | 470 | 395 | 8 |
| Mg-9Gd-3Y-0.6Zn-0.5Zr | 430 | 375 | 9.5 |
| Mg-10Gd-3Y-1Zn-0.5Zr | 428 | 339 | 4.0 |
| Mg-10Gd-6Y-2Zn-0.5Zr | 432 | 360 | 5.0 |
Table 2
| Alloy | Rm(MPa) | Rp0.2(MPa) | A (%) |
| Mg-5Gd-4Y-0.5Zn-0.4Zr | 368 | 305 | 15.3 |
| Mg-6Gd-3Y-1Zn-0.5Zr | 325 | 265 | 15.1 |
| Mg-6Gd-3Y-1.4Zn-0.5Zr | 430 | 365 | 15 |
| Mg-6Gd-3Y-1.5Zn-0.5Zr | 370 | 313 | 14 |
| Mg-6Gd-3Y-2Zn-0.5Zr | 400 | 340 | 13 |
| Mg-7Gd-4Y-0.5Zn-0.5Zr | 390 | 325 | 14 |
| Mg-7Gd-4Y-1.5Zn-0.5Zr | 448 | 390 | 12.3 |
| Mg-7Gd-4Y-2.5Zn-0.5Zr | 460 | 410 | 11.8 |
| Mg-8.2Gd-3.8Y-1Zn-0.3Zr | 471 | 385 | 12.7 |
| Mg-9Gd-3Y-0.6Zn-0.5Zr | 428 | 370 | 13.5 |
| Mg-10Gd-3Y-1Zn-0.5Zr | 430 | 340 | 11.7 |
| Mg-10Gd-6Y-2Zn-0.5Zr | 433 | 355 | 10.8 |
Contrasted by table 1 and table 2, the Mg-RE-Zn systems alloy of the phase of structure containing LPSO after the inventive method treatment,
The change amplitude of its tensile strength (Rm) and Proof strength of non-proportional (Rp0.2) is not notable, but its elongation after fracture
But it is significantly increased, therefore, the inventive method will can be closed for the Mg-RE-Zn systems alloy of all phases of structure containing LPSO
Bulk LPSO structures inversion of phases is needle-like LPSO structure phases in gold, due to the presence of needle-like LSPO structure phases so that the room of alloy
Warm plasticity is significantly improved.Additionally, this multi-step heat treatment rational technology is feasible, and it is easily real in industrialized production
It is existing.
Embodiment 3
To the as cast condition Mg-7Gd-3Y-1Nd-1Zn-0.5Zr (wt.%) in embodiment 1 two-step homogenization heat treatment after with
Stove be cooled to 440 DEG C, 450 DEG C, 460 DEG C, 470 DEG C, 480 DEG C, 490 DEG C, under 500 DEG C of temperature nodes and under above-mentioned different temperatures
Insulation 2h, remaining step is consistent with disclosed in embodiment 1, and the material to finally giving carries out mechanics properties testing, as a result such as table 3
It is shown.
Table 3
| Temperature | 440℃ | 450℃ | 460℃ | 470℃ | 480℃ | 490℃ | 500℃ |
| Sample plasticity A/% | 7.3 | 8.2 | 11.5 | 11 | 12 | 8 | 7 |
By the Data Comparison of table 3 understand it is identical in the furnace cooling time, but 440 DEG C, 450 DEG C, 490 DEG C, 500 DEG C this four
Under individual temperature nodes, plasticity changes little, but substantially lower therefore above-mentioned than at 460 DEG C, 470 DEG C, 480 DEG C of three temperature
Data Comparison explanation only can just be obviously improved the temperature-room type plasticity of material in furnace cooling temperature range of the present invention.
Embodiment 4
To the as cast condition Mg-7Gd-3Y-1Nd-1Zn-0.5Zr (wt.%) in embodiment 1 two-step homogenization heat treatment after with
Stove be cooled under 480 DEG C of temperature nodes and respectively insulation 1h30min, 1h40min, 1h50min, 2h, 2h10min, 2h20min,
2h30min, remaining step is consistent with disclosed in embodiment 1, and the material to finally giving carries out mechanics properties testing, as a result such as table
Shown in 4.
Table 4
| The furnace cooling time | 1h30min、 | 1h40min | 1h50min | 2h | 2h10min | 2h20min | 2h30min |
| Sample plasticity A/% | 8 | 8.5 | 10 | 13 | 12 | 8 | 7 |
From the experimental data of table 4, at a temperature of identical furnace cooling, 1h50min, 2h, 2h10min these three timing nodes
Under the material temperature-room type plasticity that obtains far above other four timing nodes, above-mentioned Data Comparison explanation is only cold with stove in the present invention
But time range can just be obviously improved the temperature-room type plasticity of material.
Above content is the further description done to the present invention with reference to specific embodiment, it is impossible to assert this hair
Bright specific implementation is confined to these explanations.For general technical staff of the technical field of the invention, do not taking off
On the premise of present inventive concept, some simple deduction or replace can also be made, should all be considered as belonging to protection of the invention
Scope.
Claims (9)
1. it is a kind of improve the phase of structure containing LPSO Mg-RE-Zn systems Alloy At Room Temperature plasticity method, it is characterised in that：By as cast condition Mg-
RE-Zn systems alloy carries out two-step homogenization heat treatment under conditions of 480 ± 10 DEG C × 24h+500 ± 5 DEG C × 32h, then closes
Gold is incubated 2h ± 10min at cooling to 460~480 DEG C with the furnace, obtains the Mg-RE-Zn systems alloy of the structure phases of LPSO containing needle-like.
2. the method for improving the Mg-RE-Zn systems Alloy At Room Temperature plasticity of the phase of structure containing LPSO according to claim 1, its feature
It is：The two-step homogenization heat treatment condition is 480 DEG C × 24h+500 DEG C × 32h.
3. the method for improving the Mg-RE-Zn systems Alloy At Room Temperature plasticity of the phase of structure containing LPSO according to claim 1, its feature
It is：The temperature of the alloy furnace cooling is 480 DEG C.
4. the method for improving the Mg-RE-Zn systems Alloy At Room Temperature plasticity of the phase of structure containing LPSO according to claim 3, its feature
It is：Soaking time is 2h after the alloy furnace cooling.
5. the method for improving the Mg-RE-Zn systems Alloy At Room Temperature plasticity of the phase of structure containing LPSO according to claim 1, its feature
It is：Hot extrusion step is additionally provided with after furnace cooling incubation step, quenching cooling, the heat immediately after the completion of hot extrusion step
Before pressing steps are specially extruding, by blank heating to 500 DEG C, 2~3h is incubated, during extruding, extruding rate is 0.2~2mm/s,
Extrusion ratio is 16:1.
6. the method for improving the Mg-RE-Zn systems Alloy At Room Temperature plasticity of the phase of structure containing LPSO according to claim 5, its feature
It is：Aging strengthening model is provided with after quenching cooling, aging strengthening model temperature is 200~225 DEG C, the time is 30h.
7. the method for improving the Mg-RE-Zn systems Alloy At Room Temperature plasticity of the phase of structure containing LPSO according to claim 6, its feature
It is：The aging strengthening model temperature is 200 DEG C.
8. the side of the Mg-RE-Zn systems Alloy At Room Temperature plasticity of the phase of structure containing LPSO is improved according to claim any one of 1-7
Method, it is characterised in that：The as cast condition Mg-RE-Zn systems alloy is Mg-7Gd-3Y-1Nd-1Zn-0.5Zr alloys.
9. the side of the Mg-RE-Zn systems Alloy At Room Temperature plasticity of the phase of structure containing LPSO is improved according to claim any one of 1-7
Method, it is characterised in that：The as cast condition Mg-RE-Zn systems alloy is Mg-Gd-Y-Zn-Zr alloys.
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| CN107312988A (en) * | 2017-05-27 | 2017-11-03 | 上海交通大学 | The preparation method of fine grain complex tissue containing tiny LPSO structures in magnesium alloy |
| CN107460386A (en) * | 2017-07-25 | 2017-12-12 | 上海交通大学 | A kind of magnetic field casting regulation and control magnesium alloy with high strength and ductility preparation method of structure containing LPSO |
| CN108545358A (en) * | 2018-05-03 | 2018-09-18 | 常州市第人民医院 | A kind of medical waste retracting device |
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| CN107312988A (en) * | 2017-05-27 | 2017-11-03 | 上海交通大学 | The preparation method of fine grain complex tissue containing tiny LPSO structures in magnesium alloy |
| CN107460386A (en) * | 2017-07-25 | 2017-12-12 | 上海交通大学 | A kind of magnetic field casting regulation and control magnesium alloy with high strength and ductility preparation method of structure containing LPSO |
| CN107460386B (en) * | 2017-07-25 | 2020-01-07 | 上海交通大学 | Preparation method of high-strength and high-toughness magnesium alloy containing LPSO structure through magnetic field casting regulation |
| CN108545358A (en) * | 2018-05-03 | 2018-09-18 | 常州市第人民医院 | A kind of medical waste retracting device |
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