CN104419854A - Pseudoelastic magnesium alloy, pseudoelastic magnesium alloy component, and production method thereof - Google Patents
Pseudoelastic magnesium alloy, pseudoelastic magnesium alloy component, and production method thereof Download PDFInfo
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- CN104419854A CN104419854A CN201410440375.XA CN201410440375A CN104419854A CN 104419854 A CN104419854 A CN 104419854A CN 201410440375 A CN201410440375 A CN 201410440375A CN 104419854 A CN104419854 A CN 104419854A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C23/00—Alloys based on magnesium
- C22C23/06—Alloys based on magnesium with a rare earth metal as the next major constituent
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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
- C22F1/006—Resulting in heat recoverable alloys with a memory effect
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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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- C—CHEMISTRY; METALLURGY
- C30—CRYSTAL GROWTH
- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B29/00—Single crystals or homogeneous polycrystalline material with defined structure characterised by the material or by their shape
- C30B29/10—Inorganic compounds or compositions
- C30B29/52—Alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2201/00—Treatment for obtaining particular effects
- C21D2201/01—Shape memory effect
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
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Abstract
The invention provides a pseudoelastic magnesium alloy. The pseudoelastic magnesium alloy contains magnesium as the main component thereof, and at least one element selected from Sc, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu, wherein the pseudoelastic magnesium alloy has a unidirectional crystal structure.
Description
Technical field
The present invention relates to magnesium alloy, more specifically, relate to pseudoelasticity magnesium alloy.
Background technology
In the metal being usually used in structured material etc., magnesium has minimum density.In addition, the natural resource abundant due to it and excellent recyclability, magnesium receives considerable concern as Next-generation structure material.Especially, the magnesium alloy obtained by adding various Addition ofelements to magnesium is lightweight, has the damping property of high-caliber specific tenacity and specific rigidity and excellence.Therefore, magnesium alloy is studied is used as various structured material as (such as, No. 2005-213535th, Japanese Patent Application Publication (JP 2005-213535A), No. 2006-257478th, Japanese Patent Application Publications (JP 2006-257478A)) such as the housings of auto parts, mobile electronic device.
Simultaneously, Ti-Ni series alloy appears in the newspapers as shape memory alloy with as pseudoelasticity alloy, the shape of previously memory will be turned back to when being heated to predetermined temperature after shape memory alloy is out of shape at low temperatures, obvious viscous deformation will be there is under stress in pseudoelasticity alloy, but its original shape (such as, No. 2001-262298th, Japanese Patent Application Publication (JP2001-262298A), No. 10-237572nd, Japanese Patent Application Publication (JP 10-237572)) will be turned back to when stress is unloaded.
Also appear in the newspapers, when the stress applied unloads from magnesium alloy, be out of shape and slightly reply because of the formation of twin and extinction.But, this type of degree of replying is little and be less than 0.5% (Reversible plasticstrain during cyclic loading-unloading of Mg and Mg-Zn alloys (the reversible plastix strain in the CYCLIC LOADING-uninstall process of Mg and Mg-Zn alloy), Materials Scienceand Engineering A, 456th volume, 2007,138-146 page).
Summary of the invention
As mentioned above, the various reports of existing pseudoelasticity alloy.But there is not been reported to show the magnesium alloy of pseudoelasticity.The lightweight magnesium alloy with pseudoelasticity will have wide range of application; Therefore, there are the needs developing it.Therefore, the invention provides a kind of magnesium alloy and the goods thereof with pseudoelasticity.
Present inventor has performed diligent and thorough research to obtain pseudoelasticity magnesium alloy, described pseudoelasticity magnesium alloy utilizes formation and the extinction of twin, and if be out of shape because of the stress being applied above regime of elastic deformation, then will turn back to its original shape when stress is unloaded.Result, the present inventor finds, contain element-specific by preparation and there is the magnesium alloy of the crystalline orientation of alignment, strain caused by the stress applied is prevented because of the twin formed regularly, and when stress is unloaded, strain is eliminated because of the extinction of twin, and alloy will turn back to its original shape.
Based on this understanding, the present invention relates to a kind of magnesium alloy, described magnesium alloy comprises magnesium as main ingredient and at least one element that is selected from Sc, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb and Lu, and has unidirectional crystalline structure.Because the form of the rules of twin prevents the strain from the stress applied and twin becomes extinction when stress is unloaded, the pseudoelasticity magnesium alloy of wherein strain relief can be obtained thus.
According to the present invention, can obtain use correlation technique can not obtainable pseudoelasticity magnesium alloy.
Accompanying drawing explanation
The feature of exemplary of the present invention, advantage and technology and industrial significance will hereafter describe by reference to the accompanying drawings, and in the accompanying drawings, identical Reference numeral represents identical key element, and wherein:
Fig. 1 is the stress strain diagrm of the magnesium alloy of prior art;
Fig. 2 is the photo that the twin formed in the two directions in Mg-Y monocrystalline is shown;
Fig. 3 shows and to grow with the applying of stress and to become the twin of extinction with the unloading of stress;
Fig. 4 shows the stress strain diagrm of magnesium alloy of the present invention;
Fig. 5 A shows the stress strain diagrm of the magnesium alloy (solution (solution)) of embodiment of the present invention;
Fig. 5 B is the stress strain diagrm of the magnesium alloy (timeliness 5 hours, lack time effect) of embodiment of the present invention;
Fig. 5 C is the stress strain diagrm of the magnesium alloy (timeliness 96 hours, complete timeliness) of embodiment of the present invention;
Fig. 5 D is the stress strain diagrm of the magnesium alloy (timeliness 240 hours, overaging) of embodiment of the present invention;
Fig. 6 A shows the photo of the tissue of the magnesium alloy (solution, nonageing) of embodiment of the present invention;
Fig. 6 B shows the photo of the tissue of the magnesium alloy (timeliness 5 hours) of embodiment of the present invention;
Fig. 6 C shows the photo of the tissue of the magnesium alloy (timeliness 96 hours) of embodiment of the present invention;
Fig. 6 D shows the photo of the tissue of the magnesium alloy (timeliness 240 hours) of embodiment of the present invention; With
Fig. 7 A is the stress strain diagrm of the magnesium alloy of comparative example.
Fig. 7 B is the stress strain diagrm of the magnesium alloy of comparative example.
Fig. 7 C is the stress strain diagrm of the magnesium alloy of comparative example.
Embodiment
Hereafter the present invention is described in further detail.As hereafter used, symbol " % " refers to " atom % ".The phenomenon that pseudoelasticity is eliminated with the unloading of stress for the strain wherein caused by the applying of stress.Reason is believed as follows: when being applied with the stress exceeding Hookean region, strain formation and the growth because of twin and store and but do not produce the irreversible plastix strain as relevant in basal slip with the dislocation of crystal, and when stress is eliminated, the twin being formed and grow becomes extinction.
Fig. 1 is the stress strain diagrm of the magnesium alloy of correlation technique.When to the magnesium alloy stress application of correlation technique, produce the recoverable strain 11 proportional with stress, and upon reaching the yield point, gather with dislocation as the irreversible plastix strain of basal slip thereafter, even also like this when not adding a large amount of stress.Meanwhile, due to the random formation of twin, local strain gathers 12.When stress is unloaded, the recoverable strain of storage is eliminated 13.The storage strain produced by twinnig also eliminates 14 slightly because some in formed twin become extinction.
But the amount of the strain eliminated because of the extinction of twin is little especially, does not observe large elimination.Reason is as follows: when stress application, and the formation of twin is random, and thus formed twin disturbs mutually, because the caused strains such as partial dislocation occur and become permanent, even and if stress is unloaded, and the great majority in twin also can not become extinction.In addition, once gather with the irreversible plastix strain of dislocation as basal slip, even if so stress is unloaded, eliminates and also do not occur.Therefore, obtain pseudoelasticity and need following two both conditions.
(1) if be applied for the stress being greater than critical resolved shear stress (critical resolved shear stress, CRSS) of slippage or twinnig to alloy, then slippage (dislocation) or twinnig occur.If this stress is not more than CRSS, then this will become recoverable deformation.If basal slip easily occurs in the hexagonal of magnesium when stress application, then will gather with the plastix strain owing to the dislocation of slippage, and strain will not be eliminated, even if also like this when stress is unloaded.For the strain to be canceled when stress is unloaded, when being applied with the stress exceeding Hookean region, by twin formed and strain that growth causes needs to be stored.In pseudoelasticity magnesium alloy of the present invention, select to reduce this basal slip (increasing the CRSS of basal slip) and promote that the element of twin formation (reduce the CRSS of twin or not excessively increase it) is as Addition ofelements.
Appeared in the newspapers Sc, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb and Lu for the basal slip reducing magnesium hexagonal be effective (such as, Deformation Behavior of Mg Alloy Single Crystals at VariousTemperatures (Mg alloy monocrystalline deformational behavior at different temperatures), Materials ScienceForum, 350-351 rolls up, 2000,183-188 page).Mechanism is not yet illustrated, but the interpolation of these elements can promote the formation of twin.Such as, with regard to Y, the interpolation of 1% makes the CRSS of basal slip be about 10MPa, and this is about 10 times in pure magnesium.By contrast, the CRSS of twin is about 17MPa, and this is no more than about five times than the increase of pure magnesium.In addition, in the alloy with high Y content, the CRSS of basal slip increases even more, but the CRSS of twin does not almost increase.Because the Usefulness Pair reducing basal slip and promotion twin formation is different in often kind of element, thus most suitable element can be selected as required.Element can be selected for minimizing basal slip with for promotion twin formation respectively, thus can add the element of two or more type, or the element of even three kinds or more type can be added.
For providing above-mentioned effect, these elements need to be present in matrix instead of as precipitate (such as, Mg using the form of sosoloid
24y
5).If the element of fixed amount is present in matrix with sosoloid, then it also can be used as precipitate existence simultaneously.But if with the addition of these too much elements, then in process of setting, proeutectic sosoloid will be formed in large dendritic crystal, and tiny eutectic laminate structure is formed between dendrite thereafter.If define these too much structures, then it will disturb the twin formed when stress application, and because the strain owing to dislocation motion etc. will occur, even if twin also can not become extinction when thus stress is unloaded.
Such as, when added element is Y, the upper limit that can form the amount of sosoloid is in the base 3.4%.From reducing basal slip, promoting the aspect that twinnig and dendrite are formed, treating during alloying that the amount of the Y added in matrix needs is 1.0% to 6.0%.If the amount of adding is less than 1.0%, then cannot obtain by the interpolation of Y the effect reducing basal slip and promote twin formation fully.If the amount of adding is more than 6.0%, then as mentioned above, even if stress is unloaded, twin also can not become extinction.If the amount of adding is 6.0% or less, then forms the effect of generation by minimum by dendrite, even and if a part of Y exist with precipitate, Y also can form sosoloid effectively in the base.Consider the amount that can form sosoloid in the base, the addition of Y is preferably 1.0% to 3.4%.
(2) even when defining the twin of Selective activation, if multiple twin is randomly formed, then twin disturbs mutually, and local strain (such as dislocation) occurs and becomes permanent.Therefore, even if stress is unloaded, most of twin also can not become extinction.If the formation of twin is rule and their non-interference when stress application, then partial dislocation etc. do not occur, and when stress is unloaded, larger strain relief occur because of the extinction of twin.Therefore, for making the formation of twin in magnesium alloy of the present invention be regular, crystalline orientation should be made to align in one direction.Specifically, by make crystalline structure be monocrystalline or by rolling polycrystalline alloy produce crystallographic texture crystalline orientation is alignd.
With regard to the magnesium with hexagonal crystallographic texture, relative to crystal, twin can take six different directions, but the direction of the twin formed is limited to the direction of the stress of applying.In other words, if apply stress under compression from <11-20> direction, so twin will be formed on four direction, and when compressing from <10-10> direction, twin will be formed in the two directions.In addition, when compressing from <10-1x> direction, twin will only be formed in one direction, and <10-1x> direction only tilts slightly from <10-10> direction towards the direction of c-axle.Now, it is 1 ° to 10 ° from <10-10> direction towards the angle of inclination in the direction of c-axle.In other words, optionally being formed for making twin so that their non-interference and extinction will become afterwards, first needing the crystalline orientation that aligns, then needing from specific direction stress application.
Fig. 2 shows when the structure from the twin formed in Mg-Y monocrystalline during the stress application of <10-10> direction.Can find out, the applying of stress and define multiple twin, and align in the two directions in the direction of the twin formed.Fig. 3 shows and to grow with the applying of stress and to become the twin of extinction with the unloading of stress.If they not with other interfere such as twin, crystal boundary, then stress applying and the unloading of stress is become extinction by the twin grown.
Fig. 4 shows the stress strain diagrm of magnesium alloy of the present invention.Wherein the region 41 gathered of stress application and recoverable strain is identical with the magnesium alloy of correlation technique.Region 42 trace is subsequently similar to the magnesium alloy of correlation technique, but is reduced by the plastix strain that dislocation etc. is caused, and strain is stored because of optionally regular twinnig.When stress is unloaded, recoverable strain eliminates 43 by the mode identical with the magnesium alloy in correlation technique, and the strain that this external cause twinnig is stored eliminates 44 due to the extinction of twin.But when stress application, by because of the interference with other twin, crystal boundary etc., dislocation etc. occurs in the twin that some are formed, therefore plastix strain sometimes will retain 45.
Conventional method can be used to manufacture magnesium alloy of the present invention.Magnesium alloy of the present invention has unidirectional crystalline structure (the crystal formation structure by wherein crystalline orientation alignment).The magnesium alloy wherein realizing unidirectional crystalline structure with single crystal alloy can use Bridgman method or another common manufacturing method to manufacture.In addition, wherein unidirectional crystalline structure has and has the magnesium alloy of the rolling texture of preferred orientation to obtain with crystallographic texture to control crystalline orientation by using ordinary method to produce magnesium alloy plate material, then this material of rolling.
Also ageing treatment can be applied to magnesium alloy of the present invention.If the element added is such as Y, then, when carrying out ageing treatment, compound is as Mg
24y
5to separate out.Start the stress of strain relief and the amount of elimination to regulate by the amount of precipitate because twin is withered away.The amount starting stress and the elimination eliminated can regulate according to object.But as mentioned above, the element of fixed amount needs still to be present in matrix with sosoloid, even also like this when there is precipitate.
As mentioned above, magnesium alloy of the present invention is anisotropic, and the direction number of the twin formed is different by the direction with the stress applied.When forming twin in a plurality of directions, they probably disturb mutually, and strain will retain, even if because stress is unloaded, twin also will not become extinction.Therefore, when using magnesium alloy of the present invention as parts, the direction to the stress of component end item applying becomes important.More specifically, manufacturing magnesium alloy of the present invention makes the direction of the stress under compression applied to component end item by the direction for having 10 ° or less pitch angle towards the direction of c-axle from the <10-10> direction of magnesium hexagonal.By doing like this, the twin of equal value formed will be limited to two or less type, and the interference when stress application between twin will be controlled, and thus the most advantageously can realize the pseudo-elastic effects of magnesium alloy of the present invention.
The situation wherein applying stress under compression has been described in explanation above.But much less, this is equally applicable to the situation wherein applying tensile stress along the direction near [0001] axle vertical with the direction applying above-mentioned stress under compression.
[embodiment 1]
The preparation of Bridgman method is used to have the monocrystalline of two type magnesium alloy of the material composition of Mg-0.5%Y and Mg-1.7%Y.For reducing the pollution of impurity as much as possible, make crystal in high purity graphite crucible at 50cm
3/ minute flowing argon atmosphere under grow with the growth velocity of 1mm/ hour.The crystalline orientation of magnesium alloy obtained by being confirmed by Electron Back-Scattered Diffraction (EBSD) method, and cut 3mm wide × 3mm is dark × sample that 6mm is high makes the direction of the normal direction prismatic plane of six side's magnesium crystals (normal prismatic plane) parallel with the direction of height of specimen.
For eliminating the strain being incorporated into sample in cutting process, sample stripping and slicing is placed in the silica tube with argon atmospher sealing, and carries out the strain relief annealing of five circulations by two h cycle repeated between 250 DEG C and 350 DEG C.Then sample is made at 500 DEG C, to keep 24 hours as solution thermal treatment, and last at quenching-in water.After carrying out water quenching, ageing treatment is carried out at 200 DEG C to control the amount of precipitate to some samples.The time length of ageing treatment is 5 hours, 96 hours or 240 hours.
The universal testing machine manufactured by using Instron Corporation is 2 × 10
-4apply stress under compression under the strain rate of/second along the direction of height of specimen repeatedly and then unload stress to make stress strain diagrm.The amount that the amount of strain relief obtains after being defined as and getting rid of recoverable strain component when stress is unloaded from total elimination.
Result is shown in table 1, Fig. 5 and Fig. 7 A-7C.In the sample that subjected to ageing treatment, some Y are with Mg
24y
5deng precipitation, thus in matrix, the concentration of Y is less than the concentration of Y in material composition.As shown in table 1 and Fig. 5, in the sample of embodiment numbering 11 to 14, confirm >=large the elimination of 1.9%.In addition, in the sample that subjected to ageing treatment, confirm to eliminate beginning stress different with the time length of ageing treatment.Fig. 6 A to 6D shows the Photomicrograph of embodiment.As shown in table 1 and Fig. 7 A-7C, the amount eliminated in the sample of embodiment numbering 15 to 17 is little, at≤0.25% time.In the case, the amount of elimination to be defined as when stress is 0 the size (44 of Fig. 4 with the intersection point of strain axis) of strain and the difference of the size (tangent line of 43 of Fig. 4 and the intersection point of strain axis) of the residual strain when recoverable strain is eliminated.Eliminate tangent line that the stress that starts is defined as the region (43 of Fig. 4) that wherein recoverable strain is eliminated and the stress of point of intersection of tangent line of mid point (Fig. 4 44 in be the point of 1/2 of above-mentioned amount of cancellation) that the region of eliminating wherein occurs because of pseudoelasticity.
[table 1]
Confirm the concentration of Y in matrix be wherein eliminate in the magnesium alloy of 0.5% little, but wherein in matrix the concentration of Y be 1.0% or 1.7% magnesium alloy there is the >=large elimination of 1.9%.In addition, confirm when there is precipitate because of ageing treatment, the amount eliminating stress when starting changes.
[embodiment 2]
With the amount of cancellation of the monocrystalline of Method compare Mg-1.7%Y identical with embodiment 1, the polycrystalline of Mg-1.7%Y and AZ31 rolling stock (a kind of magnesium alloy being commonly used for structured material).Monocrystalline uses method (without the ageing treatment) preparation described in embodiment 1, and polycrystalline is prepared by Regular casting methods.For AZ31 rolling stock, with the mode cutting sample identical with monocrystalline, the normal direction of prismatic plane of six side's magnesium crystals is paralleled with the direction of height of specimen, but because crystalline orientation is random in the polycrystalline material of Mg-1.7%Y, thus between the direction of prismatic plane and the direction of the height of cutting sample of six side's magnesium crystals, there is no dependency.Result is shown in Table 2.
[table 2]
The Mg-1.7%Y monocrystalline of numbering 21 shows large elimination, but both AZ31 rolling stocks of the Mg-1.7%Y polycrystalline of numbering 22 and numbering 23 have the≤little elimination value of 0.5%.With regard to Mg-1.7%Y polycrystalline, this occur reason be define twin when stress application, but due to the direction of formed twin be random, thus twin disturbs mutually, strain is formed as partial dislocation and becomes permanent, so most of twin does not become extinction with unloading.With regard to AZ31 rolling stock, this reason occurred is this structure is crystallographic texture, although and almost mutually do not disturb in formed twin, but when stress application, Al and Zn is reducing the basal slip of magnesium hexagonal and is promoting almost do not have effect in the growth of twin, and thus strain relief does not increase.
Use the present invention, can obtain use correlation technique can not obtainable pseudoelasticity magnesium alloy.
Claims (7)
1. a pseudoelasticity magnesium alloy, is characterized in that comprising:
As the magnesium of the main ingredient of described pseudoelasticity magnesium alloy; With
Be selected from least one element in Sc, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb and Lu, wherein
Described pseudoelasticity magnesium alloy has unidirectional crystalline structure.
2. pseudoelasticity magnesium alloy according to claim 1, wherein
Described unidirectional crystalline structure is monocrystalline.
3. pseudoelasticity magnesium alloy according to claim 1, wherein
Described unidirectional crystalline structure is crystallographic texture.
4. pseudoelasticity magnesium alloy according to any one of claim 1 to 3, wherein
Described pseudoelasticity magnesium alloy contains the Y of 1.0 atom % to 6.0 atom %, and
Surplus is magnesium and inevitable impurity.
5. pseudoelasticity magnesium alloy according to any one of claim 1 to 3, wherein
The matrix of described pseudoelasticity magnesium alloy contains the Y of 1.0 atom % to 3.4 atom %, and
Surplus is magnesium and inevitable impurity.
6. a pseudoelasticity magnesium alloy component, is characterized in that comprising
Pseudoelasticity magnesium alloy according to any one of claim 1 to 5, wherein
It is the direction towards the direction of c-axle from the <10-10> direction of the six side's magnesium crystals forming described pseudoelasticity magnesium alloy with 10 ° or less angle to the direction of stress under compression that component end item applies.
7. a manufacture method for pseudoelasticity magnesium alloy component, is characterized in that comprising:
Manufacturing pseudoelasticity magnesium alloy according to any one of claim 1 to 5 makes the direction of stress under compression applied to component end item be the direction towards the direction of c-axle from the <10-10> direction of the six side's magnesium crystals forming described pseudoelasticity magnesium alloy with 10 ° or less angle.
Applications Claiming Priority (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2013-181682 | 2013-09-02 | ||
| JP2013181682 | 2013-09-02 | ||
| JP2014043677A JP5913403B2 (en) | 2013-09-02 | 2014-03-06 | Magnesium alloy exhibiting pseudoelasticity, magnesium alloy part exhibiting pseudoelasticity, and method for producing the same |
| JP2014-043677 | 2014-03-06 |
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| CN104419854A true CN104419854A (en) | 2015-03-18 |
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| CN201410440375.XA Pending CN104419854A (en) | 2013-09-02 | 2014-09-01 | Pseudoelastic magnesium alloy, pseudoelastic magnesium alloy component, and production method thereof |
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| Country | Link |
|---|---|
| US (1) | US20150064053A1 (en) |
| JP (1) | JP5913403B2 (en) |
| CN (1) | CN104419854A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108603254A (en) * | 2015-10-13 | 2018-09-28 | 国立大学法人东北大学 | Show the magnesium alloy of super-elasticity effect and/or shape memory effect |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20170239386A1 (en) * | 2014-08-18 | 2017-08-24 | University Of Cincinnati | Magnesium single crystal for biomedical applications and methods of making same |
| JP6587174B2 (en) * | 2015-04-28 | 2019-10-09 | 国立研究開発法人物質・材料研究機構 | High toughness magnesium-based alloy extender and method for producing the same |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2006061960A (en) * | 2004-08-27 | 2006-03-09 | Univ Of Electro-Communications | Metallic material and method for working and producing the same |
| WO2009147861A1 (en) * | 2008-06-05 | 2009-12-10 | 独立行政法人産業技術総合研究所 | Easily formable magnesium alloy sheet and process for production thereof |
| EP2143811A1 (en) * | 2007-03-26 | 2010-01-13 | Toyota Jidosha Kabusiki Kaisha | Magnesium alloys and process for producing the same |
| WO2011118127A1 (en) * | 2010-03-23 | 2011-09-29 | 株式会社豊田自動織機 | Method for treating magnesium material and magnesium alloy member |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4154480B2 (en) * | 2002-08-08 | 2008-09-24 | 独立行政法人産業技術総合研究所 | Heat-resistant magnesium alloy and method for producing the same |
| JP5606709B2 (en) * | 2009-09-10 | 2014-10-15 | 公立大学法人大阪府立大学 | Magnesium alloy rolled material and method for producing the same |
-
2014
- 2014-03-06 JP JP2014043677A patent/JP5913403B2/en not_active Expired - Fee Related
- 2014-09-01 CN CN201410440375.XA patent/CN104419854A/en active Pending
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Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2006061960A (en) * | 2004-08-27 | 2006-03-09 | Univ Of Electro-Communications | Metallic material and method for working and producing the same |
| EP2143811A1 (en) * | 2007-03-26 | 2010-01-13 | Toyota Jidosha Kabusiki Kaisha | Magnesium alloys and process for producing the same |
| WO2009147861A1 (en) * | 2008-06-05 | 2009-12-10 | 独立行政法人産業技術総合研究所 | Easily formable magnesium alloy sheet and process for production thereof |
| JP2010013725A (en) * | 2008-06-05 | 2010-01-21 | National Institute Of Advanced Industrial & Technology | Easily formable magnesium alloy sheet and method for production thereof |
| WO2011118127A1 (en) * | 2010-03-23 | 2011-09-29 | 株式会社豊田自動織機 | Method for treating magnesium material and magnesium alloy member |
Non-Patent Citations (4)
| Title |
|---|
| G.M.MANN等: "Reversible plastic strain during cyclic loading–unloading of Mg and Mg–Zn alloys", 《MATERIALS SCIENCE AND ENGINEERING A》, 15 May 2007 (2007-05-15) * |
| S.Y.LEE等: "Pseudoelasticbehaviorofmagnesiumalloyduringtwinning-dominated cyclic deformation", 《MATERIALS SCIENCE AND ENGINEERING A》, 10 June 2013 (2013-06-10) * |
| SEIJI MIURA等: "Effect of rare-earth elements Y and Dy on the deformation behavior of Mg alloy single crystals", 《MATERIALS TRANSACTIONS》 * |
| 刘庆: "镁合金塑性变形机理研究进展", 《金属学报》, vol. 46, no. 11, 11 November 2010 (2010-11-11) * |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108603254A (en) * | 2015-10-13 | 2018-09-28 | 国立大学法人东北大学 | Show the magnesium alloy of super-elasticity effect and/or shape memory effect |
Also Published As
| Publication number | Publication date |
|---|---|
| JP5913403B2 (en) | 2016-04-27 |
| JP2015063746A (en) | 2015-04-09 |
| US20150064053A1 (en) | 2015-03-05 |
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