WO2011030474A1 - マグネシウム-リチウム合金、圧延材、成型品、およびその製造方法 - Google Patents
マグネシウム-リチウム合金、圧延材、成型品、およびその製造方法 Download PDFInfo
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- WO2011030474A1 WO2011030474A1 PCT/JP2009/071655 JP2009071655W WO2011030474A1 WO 2011030474 A1 WO2011030474 A1 WO 2011030474A1 JP 2009071655 W JP2009071655 W JP 2009071655W WO 2011030474 A1 WO2011030474 A1 WO 2011030474A1
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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
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C22/00—Chemical surface treatment of metallic material by reaction of the surface with a reactive liquid, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C22/05—Chemical surface treatment of metallic material by reaction of the surface with a reactive liquid, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using aqueous solutions
- C23C22/06—Chemical surface treatment of metallic material by reaction of the surface with a reactive liquid, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using aqueous solutions using aqueous acidic solutions with pH less than 6
- C23C22/34—Chemical surface treatment of metallic material by reaction of the surface with a reactive liquid, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using aqueous solutions using aqueous acidic solutions with pH less than 6 containing fluorides or complex fluorides
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C22/00—Chemical surface treatment of metallic material by reaction of the surface with a reactive liquid, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C22/78—Pretreatment of the material to be coated
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
- C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
- C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
- C23G1/12—Light metals
Definitions
- the present invention relates to a magnesium-lithium alloy, a rolled material, and a molded product that are excellent in corrosion resistance and cold workability.
- a rolled material of AZ31 Al 3 mass%, Zn 1 mass%, remaining Mg
- the magnesium-lithium alloy containing lithium has a magnesium crystal structure of hcp structure ( ⁇ phase), but when the lithium content is 6 to 10.5% by mass, the hcp structure and bcc structure ( ⁇ phase) When the lithium content is 10.5% by mass or more, a ⁇ -phase single phase is obtained.
- the ⁇ phase slip system is limited, but the ⁇ phase has many slip systems, so the lithium content is increased and the ⁇ phase and ⁇ phase mixed phase, the ⁇ phase single phase and As it becomes, the workability in the cold improves.
- lithium is an electrochemically base element, the corrosion resistance decreases significantly as the lithium content increases.
- alloys with high Li content such as LA141 (Li 14 mass%, Al 1 mass%, balance Mg) have been developed. However, this alloy does not have sufficient corrosion resistance and its use is limited.
- Patent Document 1 discloses that a magnesium-lithium alloy containing 10.5% by mass or less of lithium and having an iron impurity concentration of 50 ppm or less has excellent corrosion resistance.
- Patent Document 2 discloses that a magnesium-lithium alloy containing 6 to 10.5% by mass of lithium and 4 to 9% by mass of zinc is excellent in strength and corrosion resistance at room temperature.
- Patent Document 3 discloses a cold-pressable magnesium-lithium alloy containing 6 to 16% by mass of lithium.
- Patent Document 4 describes that a magnesium-lithium alloy containing 10.5 to 40% by mass of lithium and having an average crystal grain size of 3 to 30 ⁇ m is excellent in strength and press workability.
- Non-Patent Document 1 describes the effects on mechanical properties, corrosion resistance, etc. due to processing and heat treatment when Al, Zn, Cu, and Ag are added to a magnesium-lithium alloy of 8% by mass and 13% by mass of lithium. Yes.
- Patent Document 4 describes a magnesium-lithium alloy having excellent strength and press workability.
- the tensile strength of Li containing 10.5% by mass or more is at most 131 MPa. is there.
- Patent Document 4 as a method for producing a magnesium-lithium alloy excellent in strength and press workability, an ingot of a magnesium-lithium alloy raw material is hot-rolled, followed by cold-rolling, A method for recrystallizing a magnesium-lithium alloy by heat treatment at 140-150 ° C. is described. In addition, in this method, it is described that in the cold rolling, when the rolling reduction is as high as 30 to 60%, a better rolling material can be obtained than when the rolling reduction is as low as 20 to 25%. Yes. On the other hand, in the same method, if the heat treatment for recrystallizing the magnesium-lithium alloy is performed at a temperature exceeding 150 ° C., the average crystal grain size of the obtained alloy becomes too large, and the desired effect may not be obtained.
- Patent Document 4 in order to obtain a good rolled material, it is better to increase the rolling reduction of cold rolling, but if the heat treatment for recrystallization is at most 150 ° C., the strength and press It is described that a magnesium-lithium alloy excellent in workability cannot be obtained.
- the magnesium-lithium alloy as described above is considered to be used as a member constituting the housing of various electric devices such as mobile phones, notebook computers, video cameras, and digital cameras, which are expected to be lighter. ing.
- various electric devices such as mobile phones, notebook computers, video cameras, and digital cameras, which are expected to be lighter.
- it is necessary to ensure a sufficient electromagnetic shielding property or to ground the substrate, and the surface electrical resistance value of the member is required to be low.
- a magnesium-lithium alloy having a low C content has been demanded.
- JP 2000-282165 A Japanese Patent Laid-Open No. 2001-40445 Japanese Patent Laid-Open No. 9-41066 JP 11-279675 A
- An object of the present invention is to provide a very lightweight magnesium-lithium alloy, rolled material, and molded product having both high corrosion resistance and cold workability at a high level and having a certain degree of tensile strength, and a method for producing the same. It is to provide.
- the average grain size of Li is 10.5% by mass or more and 16.0% by mass or less
- Al is 0.50% by mass or more and 1.50% by mass or less
- the remainder contains Mg. Is provided
- a magnesium-lithium alloy (hereinafter, sometimes referred to as Mg-Li alloy) having a tensile strength of 150 MPa or more is provided.
- An Mg—Li alloy having a diameter of 5 ⁇ m or more and 40 ⁇ m or less and a Vickers hardness (HV) of 50 or more is provided.
- an alloy raw material melt containing 10.5 mass% or more and 16.0 mass% or less of Li, 0.50 mass% or more and 1.50 mass% or less of Al, and Mg in the balance Is cooled and solidified into an alloy ingot (a), the obtained alloy ingot is plastically processed cold so that the reduction ratio is 30% or more, and the plastically processed alloy is 170-250 And a step (c) of annealing at 250 to 300 ° C. for 10 seconds to 30 minutes at a temperature below 10 ° C. for 10 minutes to 12 hours. Furthermore, according to the present invention, a rolled material or a molded product made of the Mg—Li alloy is provided.
- the Mg—Li alloy of the present invention has a high level of both corrosion resistance and workability such as cold pressing in spite of containing 10.5% by mass or more of Li, and has a lower specific gravity than Mg. Since it contains a large amount of Li, it is excellent in practicality and can be reduced in weight.
- Li is 10.5% by mass or more and 16.0% by mass or less, preferably 13.0% by mass or more and 15.0% by mass or less, Al is 0.50% by mass or more, 1.50 mass% or less is contained, and Mg is contained in the remainder.
- Li is larger than 16% by mass, the corrosion resistance and strength of the obtained alloy are lowered and cannot be practically used.
- By containing Al within the above range mechanical strength such as tensile strength and Vickers hardness of the obtained alloy is improved.
- Al is less than 0.50 mass%, the effect of improving the mechanical strength of the obtained alloy is not sufficient.
- the Mg—Li alloy of the present invention contains Li in the above content ratio, the crystal structure is a ⁇ -phase single phase, and it is lightweight and excellent in cold workability.
- the Mg—Li alloy of the present invention further improves corrosion resistance by containing Ca in a range of 0.10% by mass to 0.50% by mass.
- Ca is contained, a compound of Mg and Ca is formed, which becomes a starting point for nucleation during recrystallization, and forms a recrystallized texture having fine crystal grains.
- Corrosion of the Mg—Li alloy proceeds selectively within the crystal grains, and the grain boundaries can prevent the progress of corrosion, and the formation of such grain boundaries can improve the corrosion resistance.
- the Mg—Li alloy of the present invention has at least one selected from Zn, Mn, Si, Zr, Ti, B, Y, a rare earth metal element having an atomic number of 57 to 71, in addition to Al and Ca described above. It can be contained in a range that does not significantly affect the corrosion resistance and cold workability. For example, when Zn is contained, the cold workability is further improved. When Mn is contained, the corrosion resistance is further improved. When Si is contained, the viscosity of the molten alloy at the time of manufacture can be lowered. Inclusion of Zr increases the strength. When Ti is contained, flame retardancy is improved.
- the strength at a high temperature is increased, but when it is contained in an amount of 1% by mass or more, the strength and the workability in the cold state are reduced.
- the rare earth metal element is contained, the elongation rate is improved and the cold workability is further improved.
- the content of these optional components is preferably 0% by mass or more and 5.00% by mass or less. If the content is large, the specific gravity increases and the characteristics of the ⁇ -phase single-phase Mg—Li alloy are impaired. Therefore, the content is preferably as small as possible.
- the Mg—Li alloy of the present invention may contain impurities such as Fe, Ni, and Cu.
- impurities such as Fe, Ni, and Cu.
- Fe is 0.005 mass% or less
- Ni is 0.005 mass% or less
- Cu is 0.005 mass% or less.
- the average crystal grain size of the Mg—Li alloy of the present invention is 5 ⁇ m or more and 40 ⁇ m or less, and the average crystal grain size is preferably 5 ⁇ m or more and 20 ⁇ m or less from the viewpoint of excellent corrosion resistance.
- the average crystal grain size is smaller than 5 ⁇ m, it is industrially difficult to obtain the Mg—Li alloy of the present invention having a tensile strength of 150 MPa or higher, or a Vickers hardness of 50 or higher, and when it exceeds 40 ⁇ m, the corrosion resistance decreases.
- the average crystal grain size can be measured by a line segment method using an observation image of an alloy cross-sectional structure with an optical microscope.
- the Mg—Li alloy of the present invention has a tensile strength of 150 MPa or more, or a Vickers hardness of 50 or more. These upper limits are not particularly limited, but the tensile strength is usually 220 MPa or less, preferably 180 MPa or less, and the Vickers hardness is usually 80 or less, preferably 70 or less, in order not to deteriorate cold workability. In the present invention, the tensile strength is determined by cutting out three JIS No. 5 test pieces each having a thickness of 1 mm in three directions of 0 °, 45 °, and 90 ° from arbitrarily determined directions of the plate material made of the Mg—Li alloy of the present invention.
- the tensile strength of the obtained test piece can be measured at 25 ° C. at a tensile speed of 10 mm / min. And each average value of 0 degree, 45 degrees, and 90 degrees directions is calculated, and those maximum values are made into tensile strength.
- the Vickers hardness is measured in accordance with JIS Z 2244, arbitrarily measured at 10 points with a load of 100 g weight at 25 ° C., and the average value is obtained.
- the present inventors have heretofore reported the average crystal grain size and the tensile strength or Vickers hardness of a ⁇ -phase single-phase Mg—Li alloy containing the above-mentioned amounts of Li and Al, such as LA141, which has been reported to have low corrosion resistance. Was found to significantly improve the corrosion resistance while maintaining good cold workability of the resulting alloy.
- the corrosion resistance of the Mg—Li alloy of the present invention exceeds the corrosion resistance of AZ31 not containing lithium, which is one of the causes of corrosion, which is currently industrialized as a plate material.
- the ⁇ -phase single-phase Mg—Li alloy containing Li and Al has been reported for many years, it has hardly been put into practical use due to low corrosion resistance.
- the -Li alloy has industrial utility.
- the above-described AZ31 that is put into practical use requires warm pressing at about 250 ° C., but the Mg—Li alloy of the present invention is excellent in cold workability and is equal to or higher than AZ31. Since it has corrosion resistance, it can be expected to be used in a wide range of fields.
- the mechanical strength of the ⁇ -phase single-phase Mg—Li alloy containing Al is not uniquely determined if its composition and average crystal grain size are determined.
- a cast slab is subjected to plastic strain by being performed at a specific reduction rate or higher, and then annealed in a specific temperature range to give a recrystallized texture.
- the average crystal grain size is 40 ⁇ m or less, high tensile strength and / or Vickers hardness that are not conventionally provided are imparted.
- Patent Document 4 the method was described in the above-mentioned Patent Document 4 in which the composition and the average crystal grain size were similar to those of the Mg—Li alloy of the present invention, which was similarly manufactured by hot rolling, cold rolling and heat treatment.
- the alloy of Example 6 has a low tensile strength of 127 MPa, and is very inferior in corrosion resistance and poor in practicality as described in Comparative Example 1 described later.
- Patent Document 4 when the average crystal grain size is increased in the Mg—Li alloy, a good rolled material cannot be obtained. Therefore, it is described in this document that the heat treatment (annealing) of the recrystallization process in which grain growth occurs cannot be performed at a temperature exceeding 150 ° C.
- annealing the heat treatment of the recrystallization process in which grain growth occurs cannot be performed at a temperature exceeding 150 ° C.
- it is considered that such conventional recognition has hindered the practical application of ⁇ -phase single-phase Mg—Li alloys for many years.
- the inventors of the present invention have provided a ⁇ -phase single-phase Mg-Li alloy containing Al, which has given a reduction ratio of a certain degree or more in cold plastic working such as cold rolling, in which the physical properties have been lowered in the annealing process. Then, by recrystallizing in a specific range at a high temperature that has been recognized, an average particle size not conventionally achieved in this composition is 5 ⁇ m or more, 40 ⁇ m or less, and a tensile strength of 150 MPa or more or a Vickers hardness of 50 or more. It has been found that the alloys shown can be obtained, and that such alloys can achieve high levels of corrosion resistance and cold workability, which are industrially practical.
- the Mg—Li alloy of the present invention is an ammeter when a probe having a cylindrical two-probe (pin contact surface area 3.14 mm 2 ) having a pin interval of 10 mm and a pin tip diameter of 2 mm is pressed against the surface with a load of 240 g.
- the surface electrical resistance value can be 1 ⁇ or less.
- the surface electric resistance value of the ammeter when this probe is pressed with a load of 60 g can be 10 ⁇ or less, and 1 ⁇ or less when adjusted to preferable conditions.
- the load of 240g assumes the fixing force when grounding to the Mg-Li alloy by screw fixing, and the load of 60g assumes the fixing force when grounding to the surface of the Mg-Li alloy by tape fixing. is doing. Therefore, when the Mg—Li alloy of the present invention is configured in this way, it can be suitably used as an electronic equipment casing component that needs to be grounded from the substrate.
- the method for producing the Mg—Li alloy of the present invention is not particularly limited as long as the Mg—Li alloy of the present invention having the above composition and physical properties can be obtained.
- the production method of the present invention shown below is mentioned.
- the production method of the present invention is an alloy raw material melt containing 10.5% by mass or more and 16.0% by mass or less of Li, 0.50% by mass or more and 1.50% by mass or less of Al, and Mg in the balance.
- the obtained alloy ingot is plastically processed cold so that the reduction ratio is 30% or more, and the plastically processed alloy is 170-250 (C) annealing at a temperature less than 10 ° C. for 10 minutes to 12 hours, or at 250 to 300 ° C. for 10 seconds to 30 minutes. If necessary, the surface of the obtained alloy is treated with aluminum and zinc metal ions.
- step (a) for example, first, a raw material in which a metal and a master alloy containing the above-mentioned optional component elements such as Mg, Li, Al, and optionally Ca, are mixed to have the above-described composition is prepared. Subsequently, the raw material can be heated and melted to obtain an alloy raw material melt, which is cast into a mold and cooled and solidified. A method of cooling and solidifying the alloy raw material melt by a continuous casting method such as a strip casting method is also preferably performed.
- the thickness of the alloy ingot (slab) obtained by the step (a) can usually be about 10 to 300 mm.
- the production method of the present invention includes a step (b) of plastically processing the alloy ingot obtained in the step (a) in a cold manner so that the reduction rate is 30% or more.
- the plastic working can be performed by a known method such as rolling, forging, extrusion, drawing, etc., and strain is given to the alloy by this plastic working.
- the temperature at that time is usually about room temperature to 150 ° C. It is preferable to carry out at room temperature or as low a temperature as possible in order to impart a large strain.
- the rolling reduction in plastic working is preferably 40% or more, more preferably 45% or more, and most preferably 90% or more, and the upper limit is not particularly limited.
- the rolling reduction is less than 30%, in the next step (c), if annealing is performed so that the tensile strength is 150 MPa or more, or the Vickers hardness is 50 or more, the average crystal of recrystallized particles as conventionally recognized The particle size becomes large and the desired effect cannot be obtained.
- the production method of the present invention includes a step (c) of annealing a cold-worked alloy at 170 to less than 250 ° C. for 10 minutes to 12 hours, or 250 to 300 ° C. for 10 seconds to 30 minutes.
- Step (c) is a step of recrystallizing the alloy to which a strain of a certain degree or more is applied in step (b).
- the annealing can be performed preferably at 190 to 240 ° C. for 30 minutes to 4 hours, or at 250 to 300 ° C. for 30 seconds to 10 minutes. If the annealing conditions are out of the range of 170-250 ° C. for 10 minutes to 12 hours, or 250-300 ° C. for 10 seconds to 30 minutes, the corrosion resistance and cold workability are reduced, and the intended practical use A highly functional Mg—Li alloy cannot be obtained.
- the production method of the present invention can include a step (a1) of subjecting the alloy ingot obtained in the step (a) to a homogeneous heat treatment before the step (b).
- the heat treatment in the step (a1) can usually be performed at 200 to 300 ° C. for 1 to 24 hours.
- the production method of the present invention can include a step (a2) of hot rolling the alloy ingot obtained in the step (a) or the step (a1) before the step (b).
- the hot rolling in step (a2) can usually be performed at 200 to 400 ° C.
- the Mg—Li alloy thus obtained is subjected to removal of the surface oxide layer or segregation layer through a degreasing step, a water washing step, etc. as necessary, as is also performed in a normal chemical conversion treatment. .
- the degreasing step can be performed by a method such as immersing in a highly alkaline solution such as sodium hydroxide.
- a highly alkaline solution such as sodium hydroxide.
- sodium hydroxide When sodium hydroxide is used, it is preferably prepared as a highly alkaline solution having a concentration of 1 to 20% by mass.
- the immersion time in the highly alkaline solution is preferably 1 to 10 minutes. If the concentration of the aqueous sodium hydroxide solution is less than 1% by mass or the immersion time is less than 1 minute, poor appearance is caused due to insufficient degreasing. Moreover, when the sodium hydroxide aqueous solution of a density
- FAL free alkalinity
- step (d) one or two or more mixed acids selected from inorganic acids (phosphoric acid, nitric acid, sulfuric acid, hydrochloric acid, hydrofluoric acid, etc.) and two metal ions (aluminum and zinc) are used. It is carried out by immersing the Mg—Li alloy in a low electrical resistance treatment solution comprising an aqueous solution to which is added. By immersing with this low electrical resistance treatment solution, an Mg—Li alloy having a low surface electrical resistance value, which has not been obtained conventionally, can be obtained. The surface electrical resistance value cannot be lowered only by adding one kind of metal of aluminum and zinc alone, and an effect can be obtained only by adding both elements.
- inorganic acids phosphoric acid, nitric acid, sulfuric acid, hydrochloric acid, hydrofluoric acid, etc.
- two metal ions aluminum and zinc
- the supply source of aluminum is supplied by a water-soluble aluminum salt such as aluminum nitrate, aluminum sulfate, or primary aluminum phosphate.
- the aluminum content in the treatment liquid is preferably 0.021 to 0.47 g / l, more preferably 0.085 to 0.34 g / l. If it is less than 0.021 g / l or exceeds 0.47 g / l, the surface electrical resistance value cannot be lowered.
- the zinc content in the treatment liquid is preferably 0.0004 to 0.029 g / l, more preferably 0.0012 to 0.013 g / l. If it is less than 0.0004 g / l, the surface electrical resistance value cannot be lowered, and if it exceeds 0.029 g / l, the surface electrical resistance value cannot be lowered, and the corrosion resistance of the film also decreases.
- the inorganic acid concentration is adjusted so that the free acidity (FA) is in the range of 9.0 to 12.0 points. If it is less than 9.0 points, it may cause insufficient processing, poor appearance, increased surface electrical resistance, decreased coating adhesion, etc. If it exceeds 12.0 points, rough skin due to excessive treatment, poor dimensionality. , Film corrosion resistance may be reduced.
- FA free acidity
- the immersion with the low electrical resistance treatment liquid in the step (d) is preferably performed at a temperature of 35 to 70 ° C., preferably 55 to 65 ° C. If it is less than 35 ° C, it may cause insufficient processing, poor appearance, increased surface electrical resistance, decreased coating adhesion, etc. If it exceeds 70 ° C, it may cause rough skin due to excessive treatment, dimensional defects, decreased corrosion resistance, etc. May occur.
- the immersion time is 0.5 to 2 minutes, more preferably 1 minute. If it is less than 0.5 minutes, the treatment may be insufficient, the surface electrical resistance value may be increased, the coating film adhesion may be decreased, and if it exceeds 2 minutes, the film corrosion resistance may be decreased.
- the surface adjustment treatment is performed with an alkaline aqueous solution.
- the surface conditioning treatment with this alkaline aqueous solution can be performed by a method such as immersing in a highly alkaline solution such as sodium hydroxide as in the degreasing step.
- sodium hydroxide it is preferably prepared as a highly alkaline solution having a concentration of 5 to 30% by mass.
- the immersion time in the highly alkaline solution is preferably 0.5 to 10 minutes.
- the immersion temperature is 45 to 70 ° C.
- the concentration of the aqueous sodium hydroxide solution is less than 5% by mass, the immersion time is less than 0.5 minutes, or the temperature is less than 45 ° C., smut may remain and the corrosion resistance of the film may decrease. is there. Further, when a sodium hydroxide aqueous solution having a concentration higher than 30% by mass is used, white powder caused by alkali residue may be generated. In addition, when using a highly alkaline solution other than the sodium hydroxide aqueous solution described above, it is preferable to use a solution adjusted so that the free alkalinity (FAL) is 31.5 to 35.5 points.
- FAL free alkalinity
- a step (e) of performing a film chemical conversion treatment with a film chemical conversion treatment liquid containing a fluoride can be performed.
- This step (e) enhances the corrosion resistance.
- the step (e) of film conversion treatment is obtained by immersing in a treatment liquid containing fluorine.
- Fluorine in this film chemical conversion treatment liquid includes hydrofluoric acid, sodium fluoride, hydrofluoric acid, acidic sodium fluoride, acidic potassium fluoride, acidic ammonium fluoride, hydrofluoric acid and its salt, and borofluoride. It is preferably supplied from at least one selected from acids and salts thereof. This is because these compounds can be obtained as a material in which fluorine is sufficiently dissolved in an active state.
- the fluorine content in the film chemical conversion treatment liquid is preferably in the range of 3.33 to 40 g / l. More preferably, it is 8.0 to 30.0 g / l. If the fluorine content is less than 3.33 g / l, the film adhesion may be insufficient and the corrosion resistance of the film may be reduced. If it exceeds 40 g / l, the surface electrical resistance increases and the adhesion to the coating film. This is because there is a possibility of causing a decrease in the amount of light.
- the acid concentration in the film chemical conversion treatment solution is adjusted so that the free acidity (FA) is in the range of 8.0 to 12.0 points. If it is less than 8.0 points, it may cause insufficient film adhesion, decrease in film corrosion resistance, etc. If it exceeds 12.0 points, it may cause an increase in surface electrical resistance and a decrease in coating film adhesion. Because there is.
- FA free acidity
- the film chemical conversion treatment with the film chemical conversion treatment liquid can be performed by a general method that allows the treatment liquid to contact the surface of the Mg—Li alloy for a certain period of time, such as immersing the Mg—Li alloy in the film chemical conversion treatment liquid. it can.
- the film chemical conversion treatment liquid is preferably carried out at a temperature of 40 to 80 ° C., preferably about 55 to 65 ° C. This is because the chemical reaction between magnesium and lithium and fluorine can be performed quickly and satisfactorily.
- the immersion time is preferably 0.5 to 5 minutes, more preferably about 1.5 to 4.5 minutes. This is because magnesium fluoride and lithium fluoride are generated on the surface of the Mg—Li alloy and the combined action is sufficiently exhibited. If the immersion time is less than 0.5 minutes, there may be insufficient film adhesion and decrease in film corrosion resistance. If it exceeds 5 minutes, the surface electrical resistance value will increase due to excessive treatment, and the film adhesion will decrease. May occur.
- the step (e) is preferably performed after the degreasing treatment, the step (d), and the surface conditioning treatment.
- a degreasing process, a process (d), a surface adjustment process, and a process (e) are each performed separately, and a water washing process is performed between each process.
- the formed coating film can have good corrosion resistance.
- This coating treatment can be performed after the surface conditioning treatment of the present invention as described above, followed by washing and drying.
- a coating method a primer treatment by epoxy cation electrodeposition coating, a top coating treatment by melamine resin or the like, or a general baking coating method can be used.
- the coating treatment process can be performed by a known method such as electrodeposition coating, spray coating, and dip coating. For example, a known organic paint or inorganic paint is used.
- an FPF (Finger Print Free) treatment glassy coating
- a heat treatment step may be appropriately performed before and after the surface treatment.
- the Mg—Li alloy obtained by the method of the present invention has excellent corrosion resistance and can reduce the surface electrical resistance value.
- it can be used in mobile phones, notebook computers, portable translators, video, etc. Effective use as various electrical equipment casing parts that require high electromagnetic shielding properties, such as cameras and digital cameras, or that require low surface electrical resistance to take the ground from the substrate. Can do.
- the Mg—Li alloy obtained by the method of the present invention can maintain excellent corrosion resistance even when it is in the state of a rolled material or even after the obtained rolled material is processed by press working or the like.
- the Mg—Li alloy in the state of the molded product after press working may be subjected to a surface treatment step after the step (c), or the Mg—Li alloy in the state of the rolled material before working may be subjected to the step ( c) Subsequent surface treatment steps may be performed.
- the rolled material of the present invention is made of the Mg—Li alloy of the present invention, it is excellent in corrosion resistance and cold workability. Usually, the rolled material has a thickness of about 0.01 to 5 mm.
- the rolled material of the present invention can be used for moldings such as portable audio equipment, digital cameras, mobile phones, laptop computers, and other automobile parts, and automobile parts by cold pressing. Since the rolled material of the present invention is excellent in cold workability, there is no cracking or poor appearance, high dimensional accuracy can be obtained, and production efficiency of the molded product or the like can be improved.
- the molded article of the present invention is excellent in corrosion resistance because it is made of the Mg—Li alloy of the present invention.
- the molded product of the present invention can be obtained by molding the Mg—Li alloy of the present invention by, for example, cutting, grinding, polishing, pressing or the like. Considering equipment and manufacturing costs, it is preferable to use the rolled material of the present invention and to perform cold pressing.
- the Mg—Li alloy obtained through all the steps described above is a cylindrical two probe (contact surface area 3.14 mm 2 of one needle) having a pin interval of 10 mm and a pin tip diameter of 2 mm (Mitsubishi Corporation).
- the surface electrical resistance value of the ammeter when the surface is pressed against the surface with a load of 240 g can be 1 ⁇ or less. Therefore, it can be suitably used as an electronic equipment casing component that needs to be grounded from the substrate or an electronic equipment casing component that requires electromagnetic shielding properties.
- Example 1 Raw materials blended so as to have a composition of Li 14.0% by mass, Al 1.00% by mass, Ca 0.30% by mass, and the balance Mg were heated and melted to obtain an alloy melt. Subsequently, this melt was cast into a 55 mm ⁇ 300 mm ⁇ 500 mm mold to produce an alloy ingot. The composition of the obtained alloy was measured by ICP analysis. The results are shown in Table 1. This alloy ingot was heat-treated at 300 ° C. for 24 hours, surface-cut, and a 50 mm thick rolling slab was produced. This slab was rolled at 350 ° C. to a plate thickness of 2 mm. Next, at room temperature, the sheet was rolled to a plate thickness of 1 mm at a reduction rate of 50% to obtain a rolled product. The obtained rolled product was annealed at 230 ° C. for 1 hour to prepare a rolled material.
- the average grain size, tensile strength, and Vickers hardness of the obtained rolled material were measured according to the methods described above.
- the corrosion resistance was evaluated by a 5% salt water immersion test. Further, cold workability was evaluated by measuring a limit drawing ratio (LDR) at room temperature. The results are shown in Table 1.
- the 5% salt water immersion test consists of 3 cycles of polishing the surface and then rinsing the acetone-washed specimen for 8 hours in salt water with a sodium chloride concentration of 5% at a liquid temperature of 25 ⁇ 5 ° C. and leaving it in the atmosphere for 16 hours. Performed by doing.
- the evaluation was performed by converting the mass change per surface area after the test as the corrosion degree, and converting the corrosion degree of the AZ31 material tested at the same time as the comparative material as 100.
- LDR measurement conditions were as follows: punch diameter: 40 mm, die diameter: 42.5 mm, die shoulder radius: 8 mm, wrinkle holding force: 12 kN, punch shoulder radius 4 mm, lubricant: molybdenum disulfide, punch speed: 3 mm / second It was.
- Comparative Example 1 A rolled material was produced in the same manner as in Example 1 except that the composition of the raw materials was Li 14.0% by mass, Al 1.00% by mass, and the balance Mg, and annealing performed at 230 ° C. for 1 hour was performed at 150 ° C. for 1 hour. And evaluated. The evaluation results are shown in Table 2.
- Examples 2 to 16 and Comparative Examples 2 to 11 A rolled material was produced in the same manner as in Example 1, except that the raw material composition was changed so that the alloy compositions shown in Table 1 and Table 2 were obtained, and the production conditions shown in Table 1 and Table 2 were changed. The obtained rolled material was evaluated in the same manner as in Example 1. Table 1 shows the results of the examples and Table 2 shows the results of the comparative examples.
- Comparative Example 2 it can be seen that although the alloy composition, tensile strength, and Vickers hardness specified for the Mg—Li alloy of the present invention are satisfied, the average crystal grain size is too large to obtain desired performance. In the comparative example 3, it turns out that it is inferior to corrosion resistance only by not containing Al as an alloy composition.
- Comparative Examples 4 and 5 when only the alloy composition with a large amount of Al or a small amount of Li is outside the range defined by the production method of the present invention, the tensile strength and Vickers hardness defined for the Mg-Li alloy of the present invention Even when the average grain size requirement is satisfied, the cold workability is remarkably inferior.
- Comparative Example 6 it can be seen that when only the alloy composition having a large amount of Li is outside the range defined by the production method of the present invention, the corrosion resistance is poor.
- Comparative Example 7 when only the annealing temperature is 1 hour at 130 ° C., which is lower than the range specified by the production method of the present invention, recrystallization does not occur, and the tensile strength and Vickers specified by the Mg—Li alloy of the present invention are achieved. It can be seen that even if the hardness requirement is satisfied, both the cold workability and the corrosion resistance are inferior.
- Comparative Example 8 when the cold reduction rate and the annealing temperature were outside the ranges specified by the production method of the present invention, recrystallization did not occur, and the tensile strength and Vickers hardness specified by the Mg-Li alloy of the present invention were not. It can be seen that even if the requirements are satisfied, both cold workability and corrosion resistance are inferior.
- Comparative Example 9 when the cold rolling reduction is out of the range specified by the production method of the present invention, the average crystal even though the tensile strength and Vickers hardness requirements specified for the Mg—Li alloy of the present invention are satisfied. It turns out that a particle size becomes large too much and is inferior to corrosion resistance.
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Abstract
Description
特許文献2には、6~10.5質量%のリチウム、4~9質量%の亜鉛を含有するマグネシウム-リチウム合金が室温での強度と耐食性に優れていることが開示されている。
特許文献3には、リチウムを6~16質量%含有する冷間プレス可能なマグネシウム-リチウム合金が開示されている。
特許文献4には、リチウムを10.5~40質量%含有し、平均結晶粒径が3~30μmのマグネシウム-リチウム合金が、強度とプレス加工性に優れることが記載されている。
非特許文献1には、リチウム8質量%と13質量%のマグネシウム-リチウム合金に、Al、Zn、Cu、Agを添加した場合の加工や熱処理による機械特性、耐食性などへの影響について記載されている。
さらに、特許文献4には、強度とプレス加工性に優れたマグネシウム-リチウム合金を製造する方法として、マグネシウム-リチウム合金原料の鋳塊を、熱間圧延し、続いて冷間圧延し、次いで、140~150℃で熱処理してマグネシウム-リチウム合金を再結晶化する方法が記載されている。
加えて、この方法において、上記冷間圧延は、圧下率を30~60%と高くした方が、圧下率20~25%と低いよりも圧延材として良好なものが得られることが記載されている。一方、同じ方法において、マグネシウム-リチウム合金を再結晶化する前記熱処理を、150℃を超える温度で実施すると、得られる合金の平均結晶粒径が大きくなりすぎて所望の効果が得られないことが記載されている。要するに、特許文献4には、良好な圧延材を得るために、冷間圧延の圧下率は高くした方が良いが、再結晶化の熱処理は、高くても150℃としなければ、強度とプレス加工性に優れたマグネシウム-リチウム合金が得られないことが記載されている。
また本発明によれば、Liを10.5質量%以上、16.0質量%以下、Alを0.50質量%以上、1.50質量%以下含有し、残部にMgを含む、平均結晶粒径が5μm以上、40μm以下、ビッカース硬度(HV)が50以上であるMg-Li合金が提供される。
更に本発明によれば、Liを10.5質量%以上、16.0質量%以下、Alを0.50質量%以上、1.50質量%以下含有し、残部にMgを含む合金原料溶融物を合金鋳塊に冷却固化する工程(a)と、得られた合金鋳塊を圧下率30%以上となるように冷間で塑性加工する工程(b)と、塑性加工した合金を170~250℃未満で10分~12時間、もしくは250~300℃で10秒~30分で焼きなましする工程(c)とを含む上記Mg-Li合金の製造方法が提供される。
更にまた本発明によれば、上記Mg-Li合金からなる圧延材又は成型品が提供される。
本発明のMg-Li合金は、Liを10.5質量%以上、16.0質量%以下、好ましくは13.0質量%以上、15.0質量%以下、Alを0.50質量%以上、1.50質量%以下含有し、残部にMgを含む。
Liが16質量%より大きいと、得られる合金の耐食性および強度が低下し実用に耐えない。Alを上記範囲内で含有させることにより、得られる合金の引張強度、ビッカース硬度等の機械強度が向上する。Alが0.50質量%より小さいと、得られる合金の機械強度を向上させる効果が十分でない。1.50質量%より大きいと、得られる合金の冷間での加工性の低下が著しい。
本発明のMg-Li合金は、Liを上記含有割合で含むので、結晶構造はβ相単相であり、軽量かつ冷間での加工性に優れる。
本発明において平均結晶粒径の測定は、合金断面組織の光学顕微鏡での観察像を用いて、線分法により行うことができる。光学顕微鏡での観察は、5%硝酸エタノールでエッチングした試料を用い、200倍で観察する。得られる観察像において、像を6等分する5本の600μmに相当する線分を引き、それを横切る粒界の数をそれぞれ測定する。線分の長さ600μmを測定した粒界の数で割った値をそれぞれの線分について算出し、その平均値を平均結晶粒径とする。
本発明において引張強度は、本発明のMg-Li合金からなる板材の任意に定めた方向から0°、45°、90°の3方向に1mm厚のJIS5号の試験片をそれぞれ3点切り出し、得られる試験片の引張強度を25℃において、引張速度10mm/分で測定することができる。そして、0°、45°、90°方向のそれぞれの平均値を算出し、それらの最大値を引張強度とする。
本発明において、ビッカース硬度は、JIS Z 2244に準拠し、25℃において100g重の荷重で任意に10箇所の測定を行い、その平均値とする。
特許文献4に記載されるとおり、Mg-Li合金において、平均結晶粒径が大きくなると良好な圧延材が得られない。従って、粒成長が生じる再結晶化工程の熱処理(焼きなまし)を、この文献では150℃を超える温度で実施することができないと記載されている。しかし、このような従来の認識が、β相単相のMg-Li合金の実用化を長年にわたり阻害してきたものと考えられる。
工程(a)により得られる合金鋳塊(スラブ)の厚さは、通常10~300mm程度とすることができる。
工程(b)において塑性加工は、例えば、圧延、鍛造、押出し、引抜き等の公知の方法で行うことができ、この塑性加工により、合金にひずみを付与する。その際の温度は、通常、室温~150℃程度である。室温かなるべく低温で行うことが、大きなひずみを付与する上で好ましい。
工程(c)は、工程(b)においてある程度以上のひずみが付与された合金を再結晶化する工程である。焼きなましは、好ましくは190~240℃で30分~4時間の条件、もしくは250~300℃で30秒~10分の条件で行うことができる。
焼きなまし条件が170~250℃未満で10分~12時間、もしくは250~300℃で10秒~30分の範囲外の場合には、耐食性及び冷間での加工性が低下し、目的とする実用性の高いMg-Li合金が得られない。
工程(a2)の熱間圧延は、通常、200~400℃により行うことができる。
皮膜化成処理する工程(e)は、フッ素を含有する処理液に浸漬することによって得られる。
上記した浸漬する方法による場合、皮膜化成処理液は、40~80℃、好ましくは約55~65℃の温度状態で行われるのが好ましい。マグネシウム及びリチウムと、フッ素との化学反応を迅速かつ良好に行わせるためである。また、浸漬時間は、好ましくは0.5~5分間、より好ましくは約1.5~4.5分間である。Mg-Li合金の表面にフッ化マグネシウム及びフッ化リチウムを生じさせると共に、その複合作用を十分に発揮させるためである。浸漬時間が0.5分間未満であると、皮膜付着量不足、皮膜耐食性低下などを生じることがあり、5分間を超えると、過剰処理のため表面電気抵抗値の上昇、塗膜密着性の低下などを生じることがある。
また、塗装処理工程は、電着塗装、スプレー塗装、浸漬塗装等の公知の方法により行うことができる。例えば、公知の有機系塗料、無機系塗料が用いられる。
さらに、表面処理の前後に適宜、熱処理の工程を行ってもよい。
さらに、本発明の方法により得られたMg-Li合金は、圧延材の状態であっても、得られた圧延材をプレス加工などで加工した後でも優れた耐食性を保つことができる。
プレス加工した後の成型品の状態になったMg-Li合金に、工程(c)以降の表面処理工程を行ってもよいし、加工前の圧延材の状態のMg-Li合金に、工程(c)以降の表面処理工程を行ってもよい。
本発明の圧延材は、冷間でのプレス加工により、例えば、携帯型のオーディオ機器、デジタルカメラ、携帯電話、ノートパソコン等の筺体や、自動車部品等の成型品に利用できる。
本発明の圧延材は、冷間での加工性に優れているため、割れや外観不良もなく、高い寸法精度が得られ、上記成型品等の生産効率を向上させることができる。
本発明の成型品は、本発明のMg-Li合金を、例えば、切削、研削、研磨、プレス等により成型することにより得ることができる。設備、製造のコストを考慮すると、本発明の圧延材を用い、冷間でのプレス加工により製造することが好ましい。
実施例1
Li14.0質量%、Al1.00質量%、Ca0.30質量%、及び残部Mgの組成となるように配合した原材料を、加熱、溶解して合金溶融物とした。続いて、この溶融物を55mm×300mm×500mmの金型中に鋳込んで合金鋳塊を作製した。得られた合金の組成をICP分析にて測定した。結果を表1に示す。
この合金鋳塊を、300℃で24時間熱処理を行い、表面切削し、厚さ50mmの圧延用スラブを作製した。このスラブを350℃にて圧延し、板厚2mmとした。次いで室温にて、圧下率50%で板厚1mmまで圧延し、圧延物を得た。得られた圧延物を230℃で1時間焼きなましして圧延材を調製した。
5%塩水浸漬試験は、表面を研磨後、アセトン洗浄した試験片を、液温度25±5℃の塩化ナトリウム濃度5%の塩水に8時間浸漬し、大気中に16時間放置する試験を3サイクル行うことにより実施した。評価は、試験後の表面積当たりの質量変化を腐食度とし、比較材として同時に試験を行ったAZ31材の腐食度を100として換算して行った。
LDRの測定条件は、パンチ径:40mm、ダイス径:42.5mm、ダイス肩半径:8mm、しわ押さえ力:12kN、パンチ肩半径4mm、潤滑剤:二硫化モリブデン、パンチスピード:3mm/秒で行った。
原材料の配合をLi14.0質量%、Al1.00質量%、残部Mgとし、230℃で1時間行った焼きなましを、150℃で1時間行った以外は、実施例1と同様に圧延材を作製し、評価を行った。評価結果を表2に示す。
表1及び表2に示す合金組成となるように原材料の配合を代え、また、表1及び表2に示す製造条件を代えた以外は、実施例1と同様に圧延材を製造した。得られた圧延材について、評価を実施例1と同様に行った。実施例の結果を表1に、比較例の結果を表2示す。
表2の結果より、比較例1及び2では、焼きなまし温度または時間のみが本発明の製造方法で規定する範囲外の場合、冷間での加工性には優れるものの耐食性に劣ることがわかる。また、比較例2では、本発明のMg-Li合金に規定する合金組成、引張強度及びビッカース硬度を満足するものの平均結晶粒径が大きすぎるために所望の性能が得られないことがわかる。
比較例3では、合金組成としてAlを含有しないのみで、耐食性に劣ることがわかる。
比較例6では、Li量が多いという合金組成のみが本発明の製造方法で規定する範囲外の場合、耐食性に劣ることがわかる。
比較例7では、焼きなまし温度のみが本発明の製造方法で規定する範囲よりも低い130℃で1時間である場合、再結晶化せず、本発明のMg-Li合金に規定する引張強度及びビッカース硬度の要件を満足していても、冷間での加工性及び耐食性のいずれにも劣ることがわかる。
比較例9では、冷間圧下率が本発明の製造方法で規定する範囲外である場合、本発明のMg-Li合金に規定する引張強度及びビッカース硬度の要件を満足していても、平均結晶粒径が大きくなりすぎ、耐食性に劣ることがわかる。
比較例10では、冷間圧下率を高くしても、焼きなまし温度が本発明の製造方法で規定する範囲よりも低い160℃で1時間である場合、再結晶化はするものの、本発明のMg-Li合金に規定する引張強度及びビッカース硬度の要件を充足せず、耐食性に劣ることがわかる。
比較例11では、冷間圧下率を高くしても、焼きなまし温度が本発明の製造方法で規定する範囲外の260℃で1時間である場合、本発明のMg-Li合金に規定する引張強度及びビッカース硬度の要件を満足していても、平均結晶粒径が大きくなりすぎて、耐食性に劣ることがわかる。
Claims (11)
- Liを10.5質量%以上、16.0質量%以下、Alを0.50質量%以上、1.50質量%以下含有し、残部にMgを含む、平均結晶粒径が5μm以上、40μm以下、引張強度が150MPa以上であるマグネシウム-リチウム合金。
- 平均結晶粒径が5μm以上、20μm以下、引張強度が150MPa以上、180MPa以下である請求項1記載のマグネシウム-リチウム合金。
- Liを10.5質量%以上、16.0質量%以下、Alを0.50質量%以上、1.50質量%以下含有し、残部にMgを含む、平均結晶粒径が5μm以上、40μm以下、ビッカース硬度(HV)が50以上であるマグネシウム-リチウム合金。
- 平均結晶粒径が5μm以上、20μm以下、ビッカース硬度(HV)が50以上、70以下である請求項3記載のマグネシウム-リチウム合金。
- Liを13.0質量%以上、15.0質量%以下含有する請求項1~4のいずれかに記載のマグネシウム-リチウム合金。
- Caを0.10質量%以上、0.50質量%以下含有する請求項1~5のいずれかに記載のマグネシウム-リチウム合金。
- Liを10.5質量%以上、16.0質量%以下、Alを0.50質量%以上、1.50質量%以下含有し、残部にMgを含む合金原料溶融物を合金鋳塊に冷却固化する工程(a)と、得られた合金鋳塊を圧下率30%以上となるように冷間で塑性加工する工程(b)と、塑性加工した合金を170~250℃未満で10分~12時間、もしくは250~300℃で10秒~30分で焼きなましする工程(c)とを含む請求項1または3記載のマグネシウム-リチウム合金の製造方法。
- 工程(a)で得られた合金鋳塊を、工程(b)の前に、均質化処理する工程(a1)を含む請求項7記載のマグネシウム-リチウム合金の製造方法。
- 工程(a)または工程(a1)で得られた合金鋳塊を、工程(b)の前に、熱間圧延する工程(a2)を含む請求項7又は8記載のマグネシウム-リチウム合金の製造方法。
- 請求項1~6のいずれかに記載のマグネシウム-リチウム合金からなる圧延材。
- 請求項1~6のいずれかに記載のマグネシウム-リチウム合金からなる成型品。
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PCT/JP2010/065655 WO2011030869A1 (ja) | 2009-09-11 | 2010-09-10 | マグネシウム-リチウム合金、圧延材、成型品、およびその製造方法 |
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TW201124541A (en) | 2011-07-16 |
CN102741436A (zh) | 2012-10-17 |
US20120222784A1 (en) | 2012-09-06 |
EP2476769B1 (en) | 2017-08-23 |
EP2476770B1 (en) | 2017-08-23 |
US20120227868A1 (en) | 2012-09-13 |
WO2011030869A1 (ja) | 2011-03-17 |
EP2476769A1 (en) | 2012-07-18 |
EP2476770A1 (en) | 2012-07-18 |
JP5643498B2 (ja) | 2014-12-17 |
CN102741436B (zh) | 2015-04-01 |
JP2011058074A (ja) | 2011-03-24 |
US9702033B2 (en) | 2017-07-11 |
CN102753714B (zh) | 2015-02-18 |
US9708700B2 (en) | 2017-07-18 |
CN102753714A (zh) | 2012-10-24 |
TWI507533B (zh) | 2015-11-11 |
EP2476769A4 (en) | 2016-09-28 |
EP2476770A4 (en) | 2016-09-28 |
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