CN103781928A - Non-heat treated magnesium alloy sheet with excellent formability at room temperature in which segregation is minimized - Google Patents
Non-heat treated magnesium alloy sheet with excellent formability at room temperature in which segregation is minimized Download PDFInfo
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- CN103781928A CN103781928A CN201280040577.4A CN201280040577A CN103781928A CN 103781928 A CN103781928 A CN 103781928A CN 201280040577 A CN201280040577 A CN 201280040577A CN 103781928 A CN103781928 A CN 103781928A
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- magnesium alloy
- segregation
- alloy plate
- heat treating
- magnesium
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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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0622—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
- B22D21/02—Casting exceedingly oxidisable non-ferrous metals, e.g. in inert atmosphere
- B22D21/04—Casting aluminium or magnesium
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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
- C22C23/02—Alloys based on magnesium with aluminium as the next major constituent
-
- 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
Abstract
The present invention relates to a non-heat treated magnesium alloy sheet which can substantially reduce casting defects such as center segregation and inverse segregation and has excellent formability when compared with a conventional commercial magnesium alloy sheet by controlling an alloy composition. The magnesium alloy sheet according to the invention comprises 1-3 wt% of Al, 0.5-3 wt% of Sn and the remaining amount of magnesium, and the difference of the mean value of Vickers hardness (Hv) caused by center segregation and inverse segregation is 10Hv or less.
Description
Technical field
The present invention relates to a kind of magnesium alloy plate of thin strap continuous casting, more specifically, relating to one can not thermal treatment (non-heat-treatable) magnesium alloy plate, it can significantly reduce the such as casting flaw such as center segregation or inverse segregation by controlling alloying constituent, and can utilize the precipitate forming in rolling shedule to control the grain growing in subsequent heat treatment program, thereby improve room temperature plasticity.
Background technology
Magnesium alloy is a kind of structured material alloy with low-gravity, high specific strength and high rigidity, and it is used as the electronics material of the such as lightweight, portable such as mobile phone and notebook computer recently more and more, or is used as automotive material to improve fuel efficiency.But, be limited to casting component for the research of magnesium alloy always.Particularly, cause sizable concern for the research improving for the high-temperature physics character of the magnesium alloy of car engine or transmission mechanism, and for example, fully do not carried out for the research that can be used for the magnesium alloy for processing (magnesium alloy plate) in field widely.
Recently, for widespread use magnesium alloy, processing is improved by the demand of magnesium-alloy material, thereby many research institutions are studied with magnesium alloy processing.Particularly, in magnesium-alloy material, the magnesium alloy plate of manufacturing by twin-roll thin strip continuous casting can be applicable to multiple fields, therefore extensively carry out for the research of magnesium alloy plate, and the present commercially available acquisition of magnesium alloy plate.
But, according to the development trend of recent magnesium alloy, owing to having added polytype alloying element or having used expensive rare earth element to develop the magnesium alloy of high strength and high-mouldability, therefore reduce price competitiveness.Therefore, up to now, unique magnesium alloy plate of manufacturing by twin-roll thin strip continuous casting is AZ31 alloy slice, and this AZ31 alloy slice has the mechanical properties that is usually used in industrial market.
Simultaneously, consider that having 200MPa is widely used in automotive industry and other outer material industries with the aluminum alloy sheet of lower yield strength (physical strength), need urgently to develop a kind of for twin-roll thin strip continuous casting can not heat treating magnesium alloys so that promptly commercialization of magnesium alloy plate improve its price competitiveness.
Summary of the invention
In sum, design the present invention and solved the problem for the conventional magnesium alloy of twin-roll thin strip continuous casting, the problem such as the low and room temperature plasticity of such as casting flaw, physical strength is poor, and the object of the present invention is to provide the one can not heat treating magnesium alloys sheet, it can reduce the casting flaws such as such as segregation by the composition of adjusting magnesium alloy, and can obtain suitable physical strength and good room temperature plasticity by the microstructure of controlling magnesium alloy, and not comprise expensive rare earth element.
For achieving the above object, an aspect of of the present present invention provides the one can not heat treating magnesium alloys sheet, and it comprises: the aluminium (Al) of 1 % by weight～3 % by weight; The tin (Sn) of 0.5 % by weight～3 % by weight; With the magnesium of surplus, wherein, average Vickers' hardness (Hv) maximum deviation being caused by center segregation and inverse segregation of described magnesium alloy product sheet is below 10Hv.
This magnesium alloy plate can form by twin-roll thin strip continuous casting, and can have Mg
2the microstructure of Sn second-phase.
In described magnesium alloy plate, Mg
2the volume ratio of Sn second-phase can be below 5%.
The yield strength of described magnesium alloy plate can be more than 200MPa, and its limit spring of arch (limit dome height, LDH) can be more than above, the preferred 6mm of 5mm.
In described magnesium alloy plate, the volume ratio that is the stretching twin of 85 °～90 ° of overturning angles with respect to master batch can be more than 5%.
Accompanying drawing explanation
Detailed description by below by reference to the accompanying drawings, above and other objects of the present invention, feature and advantage will obtain more clearly understanding, in accompanying drawing:
Fig. 1 is the schematic diagram that shows the twin-roll thin strip continuous casting equipment of manufacturing magnesium alloy plate of the present invention;
Fig. 2 is the figure that shows the thickness direction Hardness Distribution of magnesium alloy plate of the present invention and commercially available AZ31 alloy slice, and these alloy slices are divided into five equal portions separately;
Fig. 3 is the photo that shows that the composition in the cast structure cross section of magnesium alloy plate of the present invention and commercially available AZ31 alloy slice distributes, and it utilizes EPMA (electron probe X-ray microanalysis) to obtain;
Fig. 4 is the figure that shows the X-ray diffraction test result of magnesium alloy plate of the present invention;
Fig. 5 is the schematic diagram that shows the method for the limit spring of arch (LDH) of evaluating magnesium alloy plate of the present invention;
Fig. 6 is the photo that shows magnesium alloy plate of the present invention (a) and commercially available AZ31 alloy slice (b) shape after LDH tests;
Fig. 7 is the figure showing for the cross section of the sample after analysis LDH test; With
Fig. 8 is the figure that shows the crystal grain variation of magnesium alloy plate of the present invention (a) and commercially available AZ31 alloy slice (b).
Embodiment
All terms as used in this specification are all only for embodiment is described, and are not intended to limit the present invention.What in this specification sheets and claims, singulative " ", " one " and " described " used comprised plural number refers to thing, unless clear and definite referring else in context.Unless context clearly separately has needs, otherwise in whole specification sheets and claim, word " comprises " and " comprising " etc. should with comprising property implication, nonexcludability or exhaustive implication be understood, and that is to say, should understand with the meaning of " including but not limited to ".
The term that used in the specification and claims and word should not be construed as and be limited to conventional implication or the definition of dictionary, and should be interpreted as thering is the implication relevant with technical scope of the present invention and concept based on following principle, according to described principle, the concept that contriver can suitably define this term with describe known to him or she for implementing the best approach of the present invention.
Describe below with reference to the accompanying drawings the preferred embodiment of the present invention in detail.Be not intended to exhaustive or make the present invention be limited to above-disclosed precise forms for the detailed description of embodiments of the present invention above.Describing the specific embodiment of the present invention and embodiment is above for illustrative object, as the skilled person will recognize, can carry out within the scope of the present invention various equivalent modifications.
The invention provides one can not heat treating magnesium alloys sheet, and it comprises: the aluminium (Al) of 1 % by weight～3 % by weight; The tin (Sn) of 0.5 % by weight～3 % by weight; With the magnesium of surplus, wherein, average Vickers' hardness (Hv) maximum deviation being caused by center segregation and inverse segregation of described magnesium alloy plate is below 10Hv.
In sheet material casting technique, the solidification range of cast material affects segregation and the degree thereof of cast material.In the time that molten metal in plating castingprocesses solidifies moving back distance (the set back distance) district by the contracting of roller in, because sheet material is subject to the extruding of two rollers, the Bei Cong center, fluid zone coexisting in sheet material presses to surface, thereby forms the segregation line with high composition density in its surface.This phenomenon is known as " inverse segregation ".Particularly, in the situation of alloy with long solidification range, can seriously there is this inverse segregation.In the situation of aluminium alloy with relatively narrow solidification range, compared with having the situation of magnesium alloy of long solidification range, inverse segregation is not easy to occur.In addition,, even in the situation of magnesium alloy, segregation degree is also depending on the kind of alloying element and become.Due to this segregation, be difficult to control the microstructure of cast material, cast material at high temperature homogenizing very long period, the mechanical properties variation of cast material, and the surface treatment of cast material is very difficult.
For solving above segregation problem, the inventor is adjusted to the solidification range of the magnesium alloy for twin-roll thin strip continuous casting it is not had in the scope that causes deteriorated mechanical properties.As magnesium alloy of the present invention, the alloy of the magnesium of the aluminium (Al) that comprises 1 % by weight～3 % by weight, the tin (Sn) of 0.5 % by weight～3 % by weight and surplus has the solidification range of 30K～50K in the state diagram calculating with Factsage V6.2.This solidification range is equivalent to the half of the solidification range (80K～90K) of AZ31, and AZ31 is conventional twin-roll thin strip continuous casting alloy.Therefore, magnesium alloy of the present invention has the solidification range below 50K, and this is similar to aluminium alloy, has therefore significantly reduced inverse segregation.
Segregation degree can utilize the distribution of alloy composition to evaluate.In the situation of alloy with long solidification range, center segregation and inverse segregation obtain high development, and therefore, in cast structure, the center and peripheral place densification that is distributed in sheet material of alloy composition manifests.The deviation of the composition of magnesium alloy of the present invention on thickness direction do not become large.The average deviation of the AZ31 sheet of commercially available thin strap continuous casting on composition is 30%～50%, and the deviation of magnesium alloy of the present invention on composition is below 10%.
Meanwhile, generally speaking, in the time that the composition of cast material differs greatly, its hardness becomes local heterogeneity.Therefore,, when the second-phase forming when the inverse segregation by high density or center segregation district and eutectic phase flocks together, they have higher hardness.Therefore, segregation degree can be with numeral, and the maximum deviation of the average Vickers' hardness (Hv) of magnesium alloy plate of the present invention on its thickness direction can be below 10Hv.
In addition, due to Mg
2the formation of Sn second-phase, compared with the commercially available AZ31 of magnesium alloy plate of the present invention and routine, shows excellent mechanical properties.For non-heat-treatable alloy, do not adopt the thermal treatment process for controlling precipitate, the mechanism that therefore strengthens alloy physical strength is restricted.In magnesium alloy plate of the present invention, Mg
2the volume ratio of Sn second-phase is below 5%, and it is to utilize image pro plus6.0 program measure optical imagery and obtain.
Particularly, for the AZ31 with low alloyed element content, only thermal-mechanical treatment (for example hot rolling) can be as the mechanism of enhance mechanical strength.In this case, after rolling, due to grain growing and internal stress, the physical strength of AZ31 reduces rapidly along with the passage of annealing time, and this phenomenon becomes remarkable along with the rising of annealing temperature.
In magnesium alloy of the present invention, in the homogenization process of the volume ratio of second-phase after casting, greatly reduce.But second-phase is distributed in its microstructure again along with Dynamic Precipitation in the operation of rolling, and the distribution of second-phase controlling the grain growing in annealing process, prevented that thus the physical strength of magnesium alloy from reducing rapidly.
The proportion of composing of magnesium alloy is limited in to reason in above scope as follows.In the time that the amount of Al is less than 1 % by weight, improve the effect of mobility and the effect deficiency of enhancing intensity, and in the time that this amount is greater than 3 % by weight, the solidification range of the magnesium alloy of melting increases, and therefore, controls the effect deficiency of segregation.
In addition, in the time that the amount of Sn is less than 0.5 % by weight, Mg in magnesium alloy
2the volume ratio of Sn second-phase is lower, for the contribution deficiency of improving magnesium alloy mechanical properties, and in the time that this amount is greater than 3 % by weight, homogenizing treatment temp and time can increase, and the second-phase forming in the operation of rolling is distributed in aluminium alloy partly in a large number, produce negative impact to improving plasticity and elongation thus.
Conventionally, for want of slip system is and poor for magnesium plasticity at room temperature, and therefore, the deformation factor that twin is used as to replacement slip system is very important.
With conventional AZ31 alloy phase ratio, magnesium alloy plate of the present invention shows excellent room temperature formative, because stretching twin is 85 °～90 ° overturning angles with respect to master batch.
Below with reference to following examples, the present invention is described in more detail.
the manufacture of magnesium alloy plate
First, at CO
2and SF
6mixed-gas atmosphere under, use stove 10 melted pure Mg (99.9%), pure Al (99.9%) and the pure Sn (99.9%) of the twin-roll thin strip continuous casting equipment shown in Fig. 1, to prepare molten metal, then use nozzle 20 that this molten metal is injected between two cooling rollers 30, to manufacture magnesium alloy plate.In this case, distance between two cooling rollers is remained to about 2mm, in the time injecting molten metal, the rotating speed of two cooling rollers is remained to about 4m/ minute, and make the rate of cooling of molten metal remain on 200K/s～300K/s, obtain thus the magnesium alloy plate that is about 5m, wide about 70mm and thick about 2mm.
Then,, for evaluating the segregation degree of the magnesium alloy plate obtaining in its solidification range, EPMA (electron probe X-ray microanalysis) and hardness measurement have been carried out.
What Fig. 2 showed is the AZ31 sheet (comparative example) of thin strap continuous casting and the thickness direction Hardness Distribution of AT33 magnesium alloy plate (embodiment 2) of being manufactured by POSCO Corporation, wherein, the sample of long 50cm is divided into respectively to five equal portions, obtain the sample of long 10cm, then measure the hardness of each sample on its thickness direction, and be wherein, 100gf and hold-time to be to measure its Vickers' hardness under the condition of 5 seconds in load.
As shown in Figure 2, can determine that AZ31 sheet the heart and surface shows high rigidity therein partly, therefore its hardness is completely inhomogenous.By contrast, can see, AT33 sheet (embodiment 2) partly demonstrates hardness deviation to a certain degree because of segregation, but in general, the average deviation of its hardness (Hv) is below 10Hv, and the average hardness deviation that AZ31 shows is 10Hv～20Hv.Therefore, can determine, the overall hardness of AT33 sheet distributes compared with the more homogeneous of AZ31 sheet.
In addition, EPMA analytical results as shown in Figure 3 can determine, compared with AZ31 sheet, the center segregation of AT31 sheet (embodiment 1) and the degree of inverse segregation significantly reduce.In addition, can be determined by the mapping result that forms distribution of AT31 sheet and AZ31 sheet, the concentration of the composition of AZ31 sheet is the heart and near surface increase therein, and the concentration of the composition of AT31 sheet does not almost change with its thickness.Therefore, can determine, in the time that the alloy with narrower solidification range is carried out to thin strap continuous casting, the degree of its center segregation and inverse segregation reduces greatly.
thermal-mechanical treatment
As above the sheet material of manufacturing is carried out to following thermal treatment.First, this sheet material of solution-treated 3 hours at 400 ℃.Next, will be preheated to 200 ℃ through the sheet material of solution-treated, then use to be heated to the roller of 200 ℃ and to carry out hot rolling.
In course of hot rolling, 10% draft during with each hot rolling (reduction ratio) is by the sheet material hot rolling of this preheating 5 times, until final draft is 50%, finally obtains thus the sheet material that thickness is 1mm～0.7mm.
to the evaluation of mechanical properties
By above-mentioned thin strap continuous casting the annealing of heat treated magnesium alloy plate, then evaluate its mechanical properties and plasticity as shown in Table 1 below.
For evaluating the tensile properties of this magnesium alloy plate, manufacture the sample of long 12.6mm, wide 5mm and thick 1mm, be then 6.4 × 10 in deformation rate
-4s
-1the tensile properties of lower this sample of test.
In addition,, for evaluating the plasticity of this magnesium alloy plate, carried out limit spring of arch (LDH) test.Fig. 2 is the schematic diagram that shows the method for the limit spring of arch (LDH) of the magnesium alloy plate of evaluating embodiments of the present invention.In limit spring of arch (LDH) test, having manufactured diameter is the disk samples that 50mm and thickness are 0.7mm, be inserted between upper and lower mould, be then fixed between the two by the power of 5kN, and use known press oil (press oil) as lubricating oil.Next, the spherical drift that use diameter is 27.5mm makes fixing disk samples distortion with the deformation rate of 0.1mm/ second, until this disk samples is broken because of moving of drift, then measures the now Deformation Height of disk samples.
[table 1]
Be similar to AZ31 (typical non-heat-treatable alloy), this magnesium alloy plate is as can not heat treating magnesium alloys sheet, it is characterized in that, its physical strength is along with the increase of annealing time and the rising of annealing temperature and reduce, and its elongation and plasticity (, LDH) are along with the increase of annealing time and the rising of annealing temperature and improve.
Conventionally, tensile elongation is as the alternatives of plasticity, but as above given in table 1, elongation is not directly proportional to the LDH that represents plasticity utterly.Therefore, with use uniaxial extension elongation as represent plasticity index time compared with, preferably follow the test of actual forming process.
By AT alloy and conventional AZ31 alloy phase ratio, can determine to have under the condition of similar each other yield strength at the two, the plasticity of AT alloy is more excellent than conventional AZ31 alloy; And, have each other under the condition of similar LDH value, further comprise the yield strength of AT33 alloy of Sn higher than the yield strength of other AT alloys.In general, yield strength and LDH are inversely proportional to, but AT alloy has the mechanical properties more excellent than conventional ZA31 alloy, and have the LDH value higher than conventional AZ31 alloy.
What Fig. 3 showed is is presented at the photo through the shape of AT alloy slice sample after LDH test and commercially available AZ31 alloy slice sample.
Fig. 4 shows, under crystal orientation between the normal direction of sheet material and the direction of (0002) basal plane of magnesium hexagonal crystal differs from, and the top of gross distortion of each sample and the variation of the undeformed edge part of each sample.
Can be determined by Fig. 4, the texture of (0002) face is developed, and this is high because have the ratio of the poor crystal grain in low crystal orientation.This means that magnesium sheet has random structure, because difference has appearred in the crystal orientation difference of crystal grain.
As shown in Figure 4, the ratio with the poor crystal grain in high crystal orientation of magnesium alloy plate of the present invention is significantly improved.On the other hand, the ratio with the poor crystal grain in high crystal orientation of AZ31 alloy slice has raising slightly.
This difference is to be caused by the amount of the stretching twin forming in its deformation process.These stretching twins greatly contribute to improve the plasticity of the magnesium alloy plate that lacks slip system.
The invention provides a kind of magnesium alloy plate, the alloying element that described magnesium alloy plate can have a narrow solidification range by control obtains the cast structure of homogeneous, this can make up the defect being caused by segregation, and described magnesium alloy plate has excellent physical strength and plasticity, and do not use expensive rare earth element.In addition, magnesium alloy plate of the present invention can be for various Application Areass because its for can not heat treating magnesium alloys sheet and its yield strength and LDH value be linear change with annealing time.
As mentioned above, the advantage of magnesium alloy plate of the present invention is: change solidification range by adding alloying element, it can improve the defect such as such as inverse segregation and center segregation etc. occurring in the conventional magnesium alloy plate making in twin-roll thin strip continuous casting technique significantly, and, even at it through thermal treatment and after thering is high formability, its physical strength also than with routine can not thermal treatment thin strap continuous casting magnesium alloy plate physical strength excellence.
In addition, magnesium alloy plate of the present invention can show excellent plasticity, and need not add expensive rare earth element and give high formability and high strength, has therefore improved its competitive power in lightweight structural material market.
Although disclose for illustration purposes the preferred embodiment of the present invention, one skilled in the art will appreciate that and can carry out various modifications, interpolation and replacement and not depart from disclosed scope and spirit of the present invention in claims.
Claims (6)
1. can not a heat treating magnesium alloys sheet, described can not comprising by heat treating magnesium alloys sheet:
The aluminium (Al) of 1 % by weight～3 % by weight; The tin (Sn) of 0.5 % by weight～3 % by weight; With the magnesium of surplus, wherein, described average Vickers' hardness (Hv) maximum deviation being caused by center segregation and inverse segregation that can not heat treating magnesium alloys sheet is below 10Hv.
2. as claimed in claim 1 can not heat treating magnesium alloys sheet, wherein, described magnesium alloy plate forms by twin-roll thin strip continuous casting, and has Mg
2the microstructure of Sn second-phase.
3. as claimed in claim 2 can not heat treating magnesium alloys sheet, wherein, described Mg
2the volume ratio of Sn second-phase is below 5%.
As described in any one in claim 1～3 can not heat treating magnesium alloys sheet, wherein, the yield strength of described magnesium alloy plate is more than 200MPa, and limit spring of arch (LDH) is more than 5mm.
As described in any one in claim 1～3 can not heat treating magnesium alloys sheet, wherein, the yield strength of described magnesium alloy plate is more than 200MPa, and limit spring of arch (LDH) is more than 6mm.
As described in any one in claim 1～3 can not heat treating magnesium alloys sheet, wherein, the volume ratio that is the stretching twin of 85 °～90 ° of overturning angles with respect to master batch is more than 5%.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR1020110107405A KR101342582B1 (en) | 2011-10-20 | 2011-10-20 | Non heat treatable magnesium alloy sheet having less segregation and improved room temperature formability |
| KR10-2011-0107405 | 2011-10-20 | ||
| PCT/KR2012/008357 WO2013058504A2 (en) | 2011-10-20 | 2012-10-15 | Non-heat treated magnesium alloy sheet with excellent formability at room temperature in which segregation is minimized |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN103781928A true CN103781928A (en) | 2014-05-07 |
| CN103781928B CN103781928B (en) | 2016-08-17 |
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ID=48141514
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201280040577.4A Expired - Fee Related CN103781928B (en) | 2011-10-20 | 2012-10-15 | What segregation minimized at room temperature have excellent formability can not heat treating magnesium alloys sheet |
Country Status (6)
| Country | Link |
|---|---|
| US (1) | US20140205489A1 (en) |
| EP (1) | EP2770072A4 (en) |
| JP (1) | JP6099656B2 (en) |
| KR (1) | KR101342582B1 (en) |
| CN (1) | CN103781928B (en) |
| WO (1) | WO2013058504A2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109072359A (en) * | 2017-02-27 | 2018-12-21 | 韩国机械研究院 | Aging strengthening model type high-strength magnesium alloy and preparation method thereof |
| CN110031347A (en) * | 2019-04-02 | 2019-07-19 | 鞍钢股份有限公司 | A method of measurement spring steel wire rod segregation |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103290288B (en) * | 2013-06-26 | 2015-10-07 | 重庆大学 | A kind of low cost high-ductility wrought magnesium alloy and preparation method thereof |
| KR101603292B1 (en) | 2014-04-15 | 2016-03-14 | 한국신발피혁연구원 | Low specific gravity dynamic cross-linking thermoplastic elastomer for supercritical injection foaming moldingmethod producing thereof and shoe outsole using thesame |
| KR20160120688A (en) | 2016-08-29 | 2016-10-18 | 서울대학교산학협력단 | Magnesium alloy sheet and method for the same |
| WO2018155994A1 (en) * | 2017-02-27 | 2018-08-30 | 한국기계연구원 | Aging heat-treated high strength magnesium alloy and manufacturing method therefor |
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| SE452779B (en) * | 1979-09-19 | 1987-12-14 | Magnesium Elektron Ltd | APPLICATION OF A MAGNESIUM ALLOY AS ELECTRODE MATERIAL IN PRIMER CELLS |
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| JP2511526B2 (en) * | 1989-07-13 | 1996-06-26 | ワイケイケイ株式会社 | High strength magnesium base alloy |
| JP2006213983A (en) * | 2005-02-07 | 2006-08-17 | Toyota Motor Corp | Magnesium alloy bearing |
| JP5383314B2 (en) * | 2008-06-25 | 2014-01-08 | リョービ株式会社 | Creep-resistant magnesium alloy |
| JP5376507B2 (en) * | 2009-02-27 | 2013-12-25 | 独立行政法人産業技術総合研究所 | Magnesium alloy sheet having excellent cold formability and method for producing the same |
| JP5660374B2 (en) * | 2009-11-24 | 2015-01-28 | 住友電気工業株式会社 | Magnesium alloy plate manufacturing method and magnesium alloy coil material |
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-
2011
- 2011-10-20 KR KR1020110107405A patent/KR101342582B1/en not_active IP Right Cessation
-
2012
- 2012-10-15 CN CN201280040577.4A patent/CN103781928B/en not_active Expired - Fee Related
- 2012-10-15 JP JP2014536978A patent/JP6099656B2/en not_active Expired - Fee Related
- 2012-10-15 WO PCT/KR2012/008357 patent/WO2013058504A2/en active Application Filing
- 2012-10-15 EP EP12841026.3A patent/EP2770072A4/en not_active Withdrawn
- 2012-10-15 US US14/237,892 patent/US20140205489A1/en not_active Abandoned
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| JP2007138227A (en) * | 2005-11-16 | 2007-06-07 | Sumitomo Electric Ind Ltd | Magnesium alloy material |
| CN101314178A (en) * | 2007-05-28 | 2008-12-03 | 宝山钢铁股份有限公司 | Method for manufacturing gradient self-generating functional material by using double-roll thin-belt continuous casting |
| WO2010041791A1 (en) * | 2008-10-06 | 2010-04-15 | Postech Academy-Industry Foundation | Magnesium alloy panel having high formability and method of manufacturing the same |
| CN101643871A (en) * | 2009-08-24 | 2010-02-10 | 吉林大学 | Super-high-plasticity high-strength cast magnesium alloy and preparation method thereof |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109072359A (en) * | 2017-02-27 | 2018-12-21 | 韩国机械研究院 | Aging strengthening model type high-strength magnesium alloy and preparation method thereof |
| CN109072359B (en) * | 2017-02-27 | 2020-09-08 | 韩国机械研究院 | Aging heat treatment type high-strength magnesium alloy and preparation method thereof |
| CN110031347A (en) * | 2019-04-02 | 2019-07-19 | 鞍钢股份有限公司 | A method of measurement spring steel wire rod segregation |
Also Published As
| Publication number | Publication date |
|---|---|
| JP6099656B2 (en) | 2017-03-22 |
| WO2013058504A3 (en) | 2013-05-23 |
| EP2770072A4 (en) | 2015-06-17 |
| JP2014535005A (en) | 2014-12-25 |
| WO2013058504A2 (en) | 2013-04-25 |
| KR20130043355A (en) | 2013-04-30 |
| CN103781928B (en) | 2016-08-17 |
| KR101342582B1 (en) | 2013-12-17 |
| EP2770072A2 (en) | 2014-08-27 |
| US20140205489A1 (en) | 2014-07-24 |
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