CN102105613A - Cold-worked Mg-base alloy product - Google Patents
Cold-worked Mg-base alloy product Download PDFInfo
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- CN102105613A CN102105613A CN2009801285689A CN200980128568A CN102105613A CN 102105613 A CN102105613 A CN 102105613A CN 2009801285689 A CN2009801285689 A CN 2009801285689A CN 200980128568 A CN200980128568 A CN 200980128568A CN 102105613 A CN102105613 A CN 102105613A
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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
- 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
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Abstract
The invention aims at providing a cold-worked Mg-base alloy product which can bring about a remarkable lowering in the load necessary for cold plastic working and at enabling practical use of same. A cold-worked Mg-base alloy product obtained by cold-working an Mg-base alloy into a prescribed shape, characterized in that grains divided and refined by cold working are contained in the structure.
Description
Technical field
The present invention relates to be added with the Mg base alloy of lanthanide series rare-earth elements such as yttrium, relate to plastic working and be easy to Mg base alloy.
Background technology
In the past, this kind Mg base alloy was in the plastic working difficulty of cold conditions (temperature of room temperature degree) humidity province, used though therefore wish to be difficult to realize light material that structure-oriented is used etc.
Summary of the invention
The purpose of this invention is to provide the Mg base alloy cold working member that can significantly reduce the required load load of cold plasticity processing, make it can practicability.
The invention provides a kind of Mg base alloy cold working member, it is the Mg base alloy cold working member that Mg base alloy is shaped to the shape of regulation by cold working, it is characterized in that, in described tissue, contain by cold working cut apart, by refinement crystal grain.
In Mg base alloy tool member of the present invention, preferably in the Mg base alloy that constitutes, be added with one or more kinds of lanthanide series rare-earth elements.
In addition, in Mg base alloy tool member of the present invention, preferably the mean value of its crystal particle diameter is below the 30 μ m.
By having the internal structure of feature as described above, can eliminate with the AZ31 alloy is the anisotropy of the common distortion of being seen of existing deformation alloy of representative, for example, can eliminate: in the yielding stress under the situation of tension load effect is that viscous deformation begins stress and is required to be 1.2～1.4 times the shortcoming that viscous deformation under the situation of compressive load effect begins stress.
This alloy has the isotropy of distortion, for certain load, demonstrates equal deflection in all directions.Simultaneously, the needed load of deformation processing does not rely on load direction yet and is equal.
Description of drawings
Fig. 1 is the high resolving power transmission electron microscope photo that constitutes the interior tissue of this alloy (embodiment 4).
Fig. 2 is the high resolving power transmission electron microscope photo based on the Z ratio method that constitutes the interior tissue of this alloy (embodiment 4).
The last figure of Fig. 3 is for this alloy (embodiment 4), with putting the photo of representing by the existence place of the observed yttrium atom of three-dimensional atom probe; Figure below is that the existence of above figure is distributed as the basis, with gray skeleton diagram represent the yttrium atom high density partially the mode chart in zone.
Fig. 4 is the Mg-0.6 atom %Y alloy for embodiment 4, represents the graphic representation of the compression nominal stress-nominal strain relation of this alloy.
Fig. 5 be from compression testing shown in Figure 4 the direction parallel with extrusion applied compression set up to nominal strain 0.4, be that 60% alloy of initial stage height is produced test specimen, the graphic representation when similarly having carried out static compression test with the situation of Fig. 4.
Fig. 6 is the vertical section front view that is used to estimate the metal pattern assembly of cold-workability.
Fig. 7 is to use mould (jig shown in Figure 6; Anchor clamps) estimated the graphic representation of cold-workability.Express the result of the material shown in embodiment 1, embodiment 2, embodiment 4 and the comparative example 1.
Fig. 8 is the sample cross-section photograph after the shaping processing.At this, the result of press-in speed 0.03mm/ second, load 4.5 ton hours is shown.
Fig. 9 sample cross-section photograph after the processing of representing to be shaped.At this, the result of press-in speed 0.03mm/ second, load 4.5 ton hours is shown.Last figure is that AZ31 alloy, figure below are the examples of the Mg-0.6 atom %Y alloy of this alloy.
Figure 10 illustrates Mg-0.6 atom %Y 425 ℃ of down extruding and at 400 ℃ of grain orientation changes in distribution and average crystal particle diameters (d) before and after having kept 24 hours the compression set of material.At this, the interior tissue that demonstrates before being shaped and carry out forming after 4% (nominal strain 0.04), 15% (nominal strain 0.15), 25% (nominal strain 0.25) distortion.
Figure 11 illustrates and will carry out 45% (nominal strain 0.45) with the same material of Figure 10) interior tissue and the average crystal particle diameter (d) that form after the distortion.
Figure 12 illustrates and will carry out 15% (nominal strain 0.15) with the same material of Figure 10) enlarged view of the interior tissue that forms after the distortion.
Figure 13 expresses: with current material AZ31 alloy after 250 ℃ of extruding at 400 ℃ of comparative materials that kept 24 hours, with method shown in Figure 6, in patrix, carry out after the cold working variation of the tissue that forms at material internal with the speed of 0.0003mm/ second.
Figure 14 expresses: Mg-0.6 atom %Y 320 ℃ of down extruding and kept 24 hours material under 400 ℃, with method shown in Figure 6, is carried out after the cold working with the speed of 0.0003mm/ second in patrix, in the variation of the tissue of material internal formation.
Figure 15 expresses: Mg-0.1 atom %Y is pushed and kept 24 hours material at 290 ℃ under 400 ℃, with method shown in Figure 6, carry out after the cold working with the speed of 0.0003mm/ second in patrix, the variation of the tissue that forms at material internal.
Figure 16 expresses as the cold working example: Mg-0.1 atom %Y is being pushed under 290 ℃ and keeping 24 hours material and Mg-0.3 atom %Y is being pushed under 300 ℃ and kept 24 hours material under 400 ℃ under 400 ℃, with method shown in Figure 6, in patrix, carry out the interior tissue of lug (boss) the shape jut that forms after the cold working with the speed of 0.0003mm/ second and 3.0mm/ second.
Figure 17 expresses as the cold working example: Mg-0.1 atom %Y is being pushed under 290 ℃ and keeping 24 hours material and Mg-0.3 atom %Y is being pushed under 300 ℃ and kept 24 hours material under 400 ℃ under 400 ℃, with method shown in Figure 6, in patrix, carry out the interior tissue of the lug-shaped jut that forms after the cold working with the speed of 3.0mm/ second.
Figure 18 expresses as the cold working example: Mg-0.1 atom %Y is being pushed under 290 ℃ and kept 24 hours material under 400 ℃, with method shown in Figure 6, in patrix, carry out the interior tissue of the lug-shaped jut that forms after the cold working with the speed of 0.0003mm/ second.
The hardness of the jut that the position that Figure 19 and deflection are few forms after expressing with comparing and being shaped with the described cold working method of Fig. 6.
Figure 20 expresses as a comparative example: make nominal stress-nominal strain curve (last figure) that pure magnesium has been obtained when 328 ℃ of materials that push and kept under 400 ℃ 24 hours have carried out compression set, and the compression specimens of producing by mechanical workout once more after will under 0.14 nominal strain, stopping to be out of shape, along nominal stress-nominal strain curve parallel with the direction of extrusion and that obtain when having carried out compression set with the vertical direction of the direction of extrusion.
Figure 21 expresses as embodiment: make nominal stress-nominal strain curve (last figure) that Mg-0.3 atom %Y has been obtained under 400 ℃, and the compression specimens of producing by mechanical workout once more after will stopping to be out of shape under 0.40 nominal strain is along nominal stress-nominal strain curve parallel with the direction of extrusion and that obtain when having carried out compression set with the vertical direction of the direction of extrusion when the material that pushes under 300 ℃ and kept 24 hours has carried out compression set.
Figure 22 expresses as embodiment: make nominal stress-nominal strain curve (last figure) that Mg-1.0 atom %Y has been obtained under 400 ℃, and the compression specimens of producing by mechanical workout once more after stopping to be out of shape under 0.40 nominal strain is along nominal stress-nominal strain curve parallel with the direction of extrusion and that obtain when having carried out compression set with the vertical direction of the direction of extrusion when the material that pushes under 425 ℃ and kept 24 hours has carried out compression set.
Figure 23 expresses as embodiment: make nominal stress-nominal strain curve (last figure) that Mg-0.3 atom %Yb has been obtained under 450 ℃, and the compression specimens of producing by mechanical workout once more after will stopping to be out of shape under 0.40 nominal strain is along nominal stress-nominal strain curve parallel with the direction of extrusion and that obtain when having carried out compression set with the vertical direction of the direction of extrusion when the material that pushes under 300 ℃ and kept 24 hours has carried out compression set.
Figure 24 expresses as embodiment: make nominal stress-nominal strain curve (last figure) that Mg-0.3 atom %Gd has been obtained under 450 ℃, and the compression specimens of producing by mechanical workout once more after stopping to be out of shape under 0.35 nominal strain is along nominal stress-nominal strain curve parallel with the direction of extrusion and that obtain when having carried out compression set with the vertical direction of the direction of extrusion when the material that pushes under 300 ℃ and kept 24 hours has carried out compression set.
Figure 25 expresses Mg-0.6 atom %Y as a comparative example with extrusion ratio 25: 1,320 ℃ of grain structures that carried out the material of extruding of temperature.Black line among the figure is that expression crystalline orientation difference is that interface more than 5 ° is with the line as crystal boundary.
Figure 26 expresses: from what illustrate as a comparative example among Figure 25 Mg-0.6 atom %Y has been carried out the materials that push for 320 ℃ with extrusion ratio 25: 1, temperature, along parallel with the direction of extrusion and produce test specimen, and at room temperature carry out the result of compression testing with the vertical direction of the direction of extrusion.
Embodiment
In preferred mode of the present invention, its alloy structure of Mg base alloy is at 1 μ m
3Be homogeneous as a whole in the unit, but at 1 μ m
3In be dispersed with the Y high density portion that mean diameter is 2～50nm brokenly.
In preferred mode of the present invention, the Y high density portion of Mg base alloy is at 1 μ m
3The high density more than 1.5 times of the Y concentration in the unit.
The internal structure of material of the present invention is characterised in that, with 5 one-tenth of mean concns in the blank above, promptly to have to the concentration high density more than 1.5 times the zone formation mean diameter of yttrium atom be the size of 2nm～50nm, and these area with high mercury are scattered in the blank crystal grain with the interval of 2nm～50nm.
In addition, the yttrium atom that high density ground distributes does not form intermetallic compound with magnesium atom as parent phase, and promptly the structure of formation rule not though be high density, forms the distribution of random (arbitrarily).
Material of the present invention is characterized in that, is (as equivalent strain (equivalent strain more than 0.15 by applying nominal strain; Quite strain) absolute value is more than 0.17) cold working, crystal inside tissue cut apart, by refinement, is crystal particle diameters below the 30 μ m thereby have mean value.
Mg base alloy of the present invention can be made long arbitrarily bar, sheet material, bulk.Can guarantee to be considered to the cold-workability of the magnesium of difficulty in the past, can expect in all purposes, to make contributions as the lightweight structure material.
Embodiment
The making of＜alloy 〉
The fusing fully in argon atmospher with yttrium (Y) and pure magnesium (Mg) (purity 99.95%), be cast in the iron mold, producing the Y amount is 9 kinds of Mg-Y alloys of 0.1 atom %, 0.3 atom %, 0.6 atom %, 1.0 atom %, 1.2 atom %, 1.5 atom %, 2.0 atom %, 2.2 atom %, 3.0 atom %.In table 1, illustrate respectively as embodiment 1～18, comparative example 1.
Under 500 ℃ of temperature, carry out keeping in 24 hours the stove to carry out water-cooled after (atmospheric atmosphere) by the casting alloy that will obtain and implemented solution treatment.
By mechanical workout, make the cylinder material of diameter 40mm, length 70mm thereafter.
This cylinder material is being remained the container (case of each extrusion temperature shown in the table 1; Container) after (in the atmosphere) kept 30 minutes in, push at 25: 1 with extrusion ratio, thereby carried out strong strain hot-work.The average equivalent plastic strain of obtaining according to the section decrement is 3.7.
After isothermal kept 24 hours in the stove of 300～550 ℃ of temperature with this extruded material, outside stove, carry out air cooling.Extrusion temperature has adopted each temperature shown in the table 1.Average recrystallize particle diameter (μ m), stretching yield stress (A), compressive yield stress (B), yield-stress ratio (B/A), compression fracture strain have been measured.The result gathered be shown in table 1.
Table 1
Fig. 1 is the high resolving power transmission electron microscope photo that constitutes the interior tissue of this alloy.The thin point of pie graph 1 is represented the location of constituting atom.This photo is to take from the direction parallel with certain crystal face of this alloy (embodiment 4), and therefore becoming most point is the structure that atom is lined up on certain straight line.
, there is the position of part ground fall into disarray in point-like.This is because the bigger yttrium atom of atomic radius is scattered in the magnesium parent phase atom, the cause that has made as the lattice distortion of arranging unit.
And then, to concentrate brokenly by a plurality of yttrium atoms, it is remarkable that the distortion of lattice becomes.Its result has formed the zone of significantly having distorted with such lattice shown in white dashed line circle or the white dashed line ellipse as in the drawings.
Therefore, the feature of this alloy is, yttrium atom not with the structure of magnesium parent phase atom formation rule, so-called intermetallic compound, and form the area with high mercury of yttrium.
This lattice distortion the size in zone, can be from such mensuration such as electron micrograph shown in this legend.Based on the result who measures, confirm lattice distortion the average diameter size in zone: 2～50nm, disperse interval: 2～50nm.But owing in the zone of a part, find to have formed inevitable intermetallic compound, therefore yttrium atom over half forms the feature of random area with high mercury for this alloy.
In addition, the concentration of yttrium can be defined as the scope that 0.1 atom % is above, 3.0 atom % are following.
The manufacture method of blank is to wait the alloy of making the yttrium concentration that contains regulation by casting, by extruding etc., down blank is applied equivalent plastic strain 1 or more warm, carries out the isothermal maintenance 300～550 ℃ scope thereafter.
Fig. 2 is the high resolving power transmission electron microscope photo that constitutes the interior tissue of this alloy (embodiment 4).This observes photo, uses this method of Z ratio method, and as than magnesium parent phase atom, heavy atom is that the different point of yttrium atom contrast gradient is represented.For example, with the zone of white dashed line circle or white dashed line ellipse representation, the zone that a fairly large number of yttrium atom is arranged is concentrated in expression in the drawings.
These regional sizes and disperseing at interval, with shown in Fig. 1, lattice distortion zone consistent, therefore clear and definite: as the structure of the feature of this alloy, by yttrium atom high density ground and irregularly concentrate and form.
The last figure of Fig. 3 is for this alloy (embodiment 4), with putting the photo of representing by the existence place of the observed yttrium atom of three-dimensional atom probe.Figure below be above strive for survival be distributed as the basis, with gray skeleton diagram represent the yttrium atom high density partially the mode chart in zone.
At this,, show the result of the alloy of the relevant yttrium that contains 0.6 atom % as the example of alloy.
The mean concns of the yttrium in the illustration alloy is 0.6 atom %, at this, show the above concentration range of 1.0 atom %, promptly reach mean concns the concentration more than 1.67 times the zone size and distribute at interval.
The size of area with high mercury is 5～15nm, and interregional also is 5～15nm, is the same result of area with high mercury of and Fig. 2 regional with the strain of Fig. 1.
Fig. 4 is the graphic representation that shows the compression nominal stress-nominal strain relation of this alloy about the Mg-0.6 atom %Y alloy of embodiment 4.The direction of compression testing has been selected the direction parallel with the direction of extrusion of squeeze wood (180 °), with the vertical direction of this direction of extrusion (90 °), in both these 3 kinds in the direction (45 °) of intermediary.
Yielding stress, be viscous deformation to begin stress be about 60MPa, work hardening thereafter and then get gently at the gradient variable of about 0.12 times work hardening of strain is kept the state that do not rupture up to nominal strain about 0.43～0.5.Relatively the result who is out of shape along 3 kinds of directions is as can be known clear and definite, does not have the directional dependence of distortion substantially.
Orientation-independent compression set behavior as shown above is the characteristic that does not present as the AZ31 alloy of existing shape-changing material etc.
Fig. 5 be from compression testing shown in Figure 4 the direction parallel with extrusion applied compression set up to nominal strain 0.4, be that 60% alloy of initial stage height is produced test specimen, the graphic representation when similarly carrying out static compression test with the situation of Fig. 4.
Its result has applied nominal compressive strain 0.4 as can be known as initial stage strained material, and distortion beginning stress is increased to about 200MPa.In addition, as can be known clear and definite by test-results, the size of distortion beginning stress and the ratio of work hardening thereafter do not depend on the compression testing direction, are same.
In addition, along the material that the direction identical with the test direction of Fig. 4 carried out distortion, obtained the nominal breaking strain as can be known and be 0.37 big value.
Show that from above Fig. 4 and opinion shown in Figure 5 this alloy has at room temperature plastic working, is cold-workability, and the mechanical properties after the plastic working is also good.
For the cold-workability of clear and definite this alloy, use metal pattern assembly as shown in Figure 6 to estimate plastic working.
Test specimen before the distortion is the cylindrical shape of diameter 8mm, height 6mm, is placed in the counterdie of tool steel in the cylindrical cross-section hole with same diameter.Thereafter, make above the test specimen and contact with the patrix of the cylindrical cross-section hole that has diameter 3mm at central shaft with the R portion that has radius 1.Smm at shoulder, move patrix by the face of facing down from figure, make the test specimen of being restrained by counterdie carry out plastic flow, confirmed plasticity thus along the centre hole that is arranged at patrix.In addition, in the surface coated of test specimen and metal pattern silicone grease be used as lubricant.
In the process of forming test, the required load load that measure to be shaped and on the amount of being molded into, be used as the index of plasticity.
If the plasticity of blank is abundant, then be configured as the outstanding shape of lug of the diameter identical as shown in Figure 6 with patrix, therefore can directly confirm plasticity and follow to be processed with and do not have the crackle of formation by the cross-section after the processing.
Fig. 7 is to use mould shown in Figure 6 to estimate the graphic representation of cold-workability.
As test specimen, show as the Mg-0.6 atom %Y of Mg-0.3 atom %Y, the embodiment 4 of Mg-0.1 atom %Y, the embodiment 2 of the embodiment 1 of the example of this alloy and under identical conditions, use AZ31 alloy 1 result as a comparative example.
At this,, selected 0.0003mm/ second, 0.03mm/ second as the press-in speed of patrix.
In addition, in this test, the ultimate load that gives is made as 4.5 tons (45kN).
By load and the relation that is pressed into displacement obviously as can be known, be used to obtain the required load of shaping of this alloy of identical forming height, compare with the situation of current material AZ31, low about 2 one-tenth～4 one-tenth.
Fig. 8 sample cross-section photograph after the processing of representing to be shaped.At this, show the result of 4.5 tons of press-in speed 0.0003mm/ seconds, load.Last figure is the situation of the AZ31 alloy shown in the comparative example 1, and the forming height that comprises R portion is 1.8mm.
Figure below is the example of the Mg-0.6 atom %Y alloy of this alloy (embodiment 4), and forming height is 3.7mm, has obtained the forming height more than 2 times of AZ31 alloy, has confirmed the plasticity of this alloy.
Fig. 9 sample cross-section photograph after the processing of representing to be shaped.At this, show the result of 4.5 tons of press-in speed 0.03mm/ seconds, load.Last figure, in the occasion of the AZ31 alloy shown in the comparative example 1, the forming height that comprises R portion is 1.4mm.Figure below is the example of the Mg-0.6 atom %Y alloy of this alloy (embodiment 4), and forming height is 2.9mm, has obtained the forming height more than 2 times of AZ31 alloy, has confirmed the plasticity of this alloy.
Below, by representing the further data of above-mentioned crystalline distortion, express the reason that cold worked real attitude and intensity increase therefrom.Example is expressed the boundary of the numerical value that produces this phenomenon by experiment.In addition, for the rare earth element beyond the Y, demonstrate and also cause same phenomenon.
Figure 10 represents Mg-0.6 atom %Y is being pushed under 425 ℃ and kept grain orientation changes in distribution and average crystal particle diameter before and after 24 hours the compression set of material under 400 ℃.At this, the interior tissue that shows before shaping and carry out 4% (nominal strain 0.04), 15% (nominal strain 0.15), 25% (nominal strain 0.25) distortion back formation.Applied the material of the distortion of nominal strain more than 0.15, with the material compared before the distortion, the average crystalline particle diameter is below the 30 μ m, by refinement.
Figure 11 represent will with the same material of Figure 10 through 45% (nominal strain 0.45)) interior tissue of distortion back formation.Boundary line shown in the black line among the figure, it is that the above situation of 5 degree is as crystal boundary that the crystalline orientation difference is shown.Compare as can be known with organizing before the distortion shown in Figure 10, it is 1/5 that crystal particle diameter is refined into.
Figure 12 represent will with the same material of Figure 10 through 15% (nominal strain 0.15)) enlarged view of the interior tissue of distortion back formation.The L and the crystalline orientation on the line shown in the T that show among the figure with the solid line of right figure change.The deep or light position that has taken place to change, the dawn among for example figure position shown in the arrow, expressing orientation angle from the bottom right graphic representation has increased by 5 degree.Promptly proved: cold working member of the present invention, by implementing cold working, variation has taken place in the orientation of the crystal grain inside that has, along with the strained that gives increases, it is big that the crystalline orientation difference becomes, and forms crystal boundary soon, crystal grain is cut off thus, and the average crystalline particle diameter of material internal is by refinement.
Figure 13 represents and will push the comparative material that the back has kept 24 hours at 250 ℃ under 400 ℃ as the AZ31 alloy of current material, with method shown in Figure 6, in patrix, carry out after the cold working variation of the tissue that forms at material internal with 0.0003mm/ speed second.At the central part D of work material, do not see the partition of crystal grain, the distortion twin as banded structure along oblique formation.
Figure 14 represents Mg-0.6 atom %Y is pushed at 320 ℃, has kept 24 hours material under 400 ℃,, carries out after the cold working variation of the tissue that forms at material internal in patrix with method shown in Figure 6 with 0.0003mm/ speed second.At the central part D of work material, do not form banded structure, and formed new crystal boundary as can be known to random direction to the specific direction as the distortion twin.
Figure 15 represents Mg-0.1 atom %Y is pushed under 290 ℃, has kept 24 hours material under 400 ℃,, carries out after the cold working variation of the tissue that forms at material internal in patrix with method shown in Figure 6 with 0.0003mm/ speed second.At the central part D of work material, do not form banded structure, and formed new crystal boundary as can be known to random direction to the specific direction as the distortion twin.
Figure 16 expresses as the cold working example: Mg-0.1 atom %Y is being pushed under 290 ℃ and keeping 24 hours material and Mg-0.3 atom %Y is being pushed under 300 ℃ and kept 24 hours material under 400 ℃ under 400 ℃, with method shown in Figure 6, in patrix, carry out the interior tissue of the lug-shaped jut that forms after the cold working with the speed of 0.0003mm/ second and 3.0mm/ second.
Figure 17 expresses as the cold working example: Mg-0.1 atom %Y is being pushed under 290 ℃ and keeping 24 hours material and Mg-0.3 atom %Y is being pushed under 300 ℃ and kept 24 hours material under 400 ℃ under 400 ℃, with method shown in Figure 6, in patrix, carry out the cold working interior tissue of the lug-shaped jut of formation afterwards with 3.0mm/ speed second.Express the tissue at the position shown in the D among the deformation pattern figure of Figure 13.Under the speed 3.0mm/ process velocity of second, cause same grain refining as can be known.
Figure 18 expresses as the cold working example: make Mg-0.1 atom %Y is being pushed under 290 ℃ and kept 24 hours material under 400 ℃, with method shown in Figure 6, in patrix, carry out the cold working interior tissue of the lug-shaped jut of formation afterwards with 0.0003mm/ speed second.By the distribution of orientations figure of distortion back tissue as can be known grain structure by refinement.
Figure 19 adopts the hardness of the jut that the described cold working method of Fig. 6 forms after being shaped as can be known, and comparing with the few position of deflection has increased.The refinement of the crystal grain that is produced by cold working has brought the intensity increase as can be known.
Figure 20 expresses as a comparative example: make nominal stress-nominal strain curve (last figure) that pure magnesium has been obtained when 328 ℃ of materials that push and kept under 400 ℃ 24 hours have carried out compression set, and the compression specimens of producing by mechanical workout once more after will under 0.14 nominal strain, stopping to be out of shape, along nominal stress-nominal strain curve parallel with the direction of extrusion and that obtain when having carried out compression set with the vertical direction of the direction of extrusion.Yield strength is different greatly, can see ANISOTROPIC DEFORMATION.
Figure 21 expresses as embodiment: make nominal stress-nominal strain curve (last figure) that Mg-0.3 atom %Y has been obtained under 400 ℃, and the compression specimens of producing by mechanical workout once more after will stopping to be out of shape under 0.40 nominal strain is along nominal stress-nominal strain curve parallel with the direction of extrusion and that obtain when having carried out compression set with the vertical direction of the direction of extrusion when the material that pushes under 300 ℃ and kept 24 hours has carried out compression set.The anisotropy that can confirm yield strength has reduced.
Figure 22 expresses as embodiment: make nominal stress-nominal strain curve (last figure) that Mg-1.0 atom %Y has been obtained under 400 ℃, and the compression specimens of producing by mechanical workout once more after will stopping to be out of shape under 0.40 nominal strain is along nominal stress-nominal strain curve parallel with the direction of extrusion and that obtain when having carried out compression set with the vertical direction of the direction of extrusion when the material that pushes under 425 ℃ and kept 24 hours has carried out compression set.The anisotropy that can confirm yield strength has reduced.
Figure 23 expresses as embodiment: make nominal stress-nominal strain curve (last figure) that Mg-0.3 atom %Yb has been obtained under 450 ℃, and the compression specimens of producing by mechanical workout once more after will stopping to be out of shape under 0.40 nominal strain is along nominal stress-nominal strain curve parallel with the direction of extrusion and that obtain when having carried out compression set with the vertical direction of the direction of extrusion when the material that pushes under 300 ℃ and kept 24 hours has carried out compression set.The anisotropy that can confirm yield strength and work hardening rate has reduced.
Figure 24 expresses as embodiment: make nominal stress-nominal strain curve (last figure) that Mg-0.3 atom %Gd has been obtained under 450 ℃, and the compression specimens of producing by mechanical workout once more after will stopping to be out of shape under 0.35 nominal strain is along nominal stress-nominal strain curve parallel with the direction of extrusion and that obtain when having carried out compression set with the vertical direction of the direction of extrusion when the material that pushes under 300 ℃ and kept 24 hours has carried out compression set.The anisotropy that can confirm yield strength and work hardening rate has reduced.
Figure 25 expresses Mg-0.6 atom %Y as a comparative example with extrusion ratio 25: 1,320 ℃ of grain structures that carried out the material of extruding of temperature.Black line among the figure is that expression crystalline orientation difference is that interface more than 5 ° is with the line as crystal boundary.With embodiment shown in Figure 11 more as can be known, organize after the cold working of this comparative example, left part in the drawings and central part are cut apart insufficient and remaining thick grain structure that has.
Figure 26 expresses: from what illustrate as a comparative example among Figure 25 Mg-0.6 atom %Y has been carried out the materials that push for 320 ℃ with extrusion ratio 25: 1, temperature, along parallel with the direction of extrusion and produce test specimen, and at room temperature carry out the result of compression testing with the vertical direction of the direction of extrusion.Nominal strain during fracture is below 0.13, though have and Fig. 4 and the same composition of present embodiment alloy shown in Figure 5, cold-workability is low.In addition, work hardening rate after the surrender, according to the sample preparation direction and different greatly, and, nominal stress before being about to when having carried out compression testing along the direction parallel with the direction of extrusion ruptured, with compare with the situation of the vertical direction of the direction of extrusion, demonstrate value near 2 times, therefore ANISOTROPIC DEFORMATION is stronger as can be known.
Utilize possibility on the industry
According to the present invention, the Mg base alloy cold working member of the load load that can significantly reduce cold plasticity machining need can be provided, it can be practical.
Claims (4)
1. Mg base alloy cold working member is the Mg base alloy cold working member that Mg base alloy is shaped to the shape of regulation by cold working, it is characterized in that, in described tissue, contain by cold working cut apart, by refinement crystal grain.
2. Mg base alloy cold working member according to claim 1 is characterized in that, is added with one or more kinds of lanthanide series rare-earth elements in the Mg base alloy that constitutes.
3. Mg base alloy cold working member according to claim 1 and 2 is characterized in that the mean value of its crystal particle diameter is below the 30 μ m.
4. Mg according to claim 1 and 2 base alloy cold working member is characterized in that, is equivalent strain more than 0.17 (the nominal compressive strain is 0.15) having given as absolute value by cold working under the temperature below 150 ℃ such as room temperature.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP188397/2008 | 2008-07-22 | ||
| JP2008188397 | 2008-07-22 | ||
| PCT/JP2009/063452 WO2010010965A1 (en) | 2008-07-22 | 2009-07-22 | COLD-WORKED Mg-BASE ALLOY PRODUCT |
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| CN102105613A true CN102105613A (en) | 2011-06-22 |
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| US (1) | US20110135532A1 (en) |
| EP (1) | EP2319949B1 (en) |
| JP (1) | JP5549981B2 (en) |
| CN (1) | CN102105613A (en) |
| WO (1) | WO2010010965A1 (en) |
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| EP2835437B1 (en) * | 2012-05-31 | 2017-09-06 | National Institute for Materials Science | Magnesium alloy, magnesium alloy member and method for manufacturing same, and method for using magnesium alloy |
| ES2829376T3 (en) | 2013-03-14 | 2021-05-31 | Univ Erasmus Med Ct Rotterdam | Non-human mammal transgenic for antibody production |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1980759A (en) * | 2004-06-30 | 2007-06-13 | 住友电气工业株式会社 | Method for producing magnesium alloy product |
| US20080017285A1 (en) * | 2004-06-30 | 2008-01-24 | National Institute For Materials Science | Magnesium Alloy Exhibiting High Strength and High Ductility and Method for Production Thereof |
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| JPH0941066A (en) * | 1995-08-01 | 1997-02-10 | Mitsui Mining & Smelting Co Ltd | Magnesium alloy capable of cold press working |
| JP4776751B2 (en) * | 2000-04-14 | 2011-09-21 | パナソニック株式会社 | Magnesium alloy sheet manufacturing method |
| JP2003328065A (en) * | 2002-05-10 | 2003-11-19 | Toyo Kohan Co Ltd | Wrought magnesium thin-sheet superior in formability, and manufacturing method therefor |
| EP1959025B1 (en) * | 2005-11-16 | 2012-03-21 | National Institute for Materials Science | Magnesium-based biodegradable metal material |
| JP5252363B2 (en) * | 2007-02-28 | 2013-07-31 | 独立行政法人産業技術総合研究所 | Magnesium alloy press-molded body and method for producing the same |
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- 2009-07-22 CN CN2009801285689A patent/CN102105613A/en active Pending
- 2009-07-22 US US13/055,214 patent/US20110135532A1/en not_active Abandoned
- 2009-07-22 EP EP09800476.5A patent/EP2319949B1/en not_active Not-in-force
- 2009-07-22 JP JP2010521754A patent/JP5549981B2/en not_active Expired - Fee Related
- 2009-07-22 WO PCT/JP2009/063452 patent/WO2010010965A1/en active Application Filing
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1980759A (en) * | 2004-06-30 | 2007-06-13 | 住友电气工业株式会社 | Method for producing magnesium alloy product |
| US20080017285A1 (en) * | 2004-06-30 | 2008-01-24 | National Institute For Materials Science | Magnesium Alloy Exhibiting High Strength and High Ductility and Method for Production Thereof |
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| JP5549981B2 (en) | 2014-07-16 |
| JPWO2010010965A1 (en) | 2012-01-05 |
| EP2319949B1 (en) | 2015-02-18 |
| EP2319949A4 (en) | 2012-12-12 |
| WO2010010965A1 (en) | 2010-01-28 |
| EP2319949A1 (en) | 2011-05-11 |
| US20110135532A1 (en) | 2011-06-09 |
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