CN110785506A - Magnesium alloy sheet material and method for producing same - Google Patents
Magnesium alloy sheet material and method for producing same Download PDFInfo
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- CN110785506A CN110785506A CN201880042004.2A CN201880042004A CN110785506A CN 110785506 A CN110785506 A CN 110785506A CN 201880042004 A CN201880042004 A CN 201880042004A CN 110785506 A CN110785506 A CN 110785506A
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- 229910000861 Mg alloy Inorganic materials 0.000 title claims abstract description 156
- 239000000463 material Substances 0.000 title claims abstract description 124
- 238000004519 manufacturing process Methods 0.000 title abstract description 20
- 239000011777 magnesium Substances 0.000 claims abstract description 31
- 239000012535 impurity Substances 0.000 claims abstract description 16
- 238000005096 rolling process Methods 0.000 claims description 68
- 239000013078 crystal Substances 0.000 claims description 52
- 239000002245 particle Substances 0.000 claims description 34
- 238000005204 segregation Methods 0.000 claims description 28
- 239000011575 calcium Substances 0.000 description 54
- 235000013339 cereals Nutrition 0.000 description 45
- 238000010438 heat treatment Methods 0.000 description 29
- 230000000052 comparative effect Effects 0.000 description 27
- 238000005266 casting Methods 0.000 description 23
- 230000009467 reduction Effects 0.000 description 20
- 239000011572 manganese Substances 0.000 description 18
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 17
- 238000000034 method Methods 0.000 description 17
- 239000011701 zinc Substances 0.000 description 17
- 238000005098 hot rolling Methods 0.000 description 14
- 229910052749 magnesium Inorganic materials 0.000 description 14
- 239000000155 melt Substances 0.000 description 13
- AZUYLZMQTIKGSC-UHFFFAOYSA-N 1-[6-[4-(5-chloro-6-methyl-1H-indazol-4-yl)-5-methyl-3-(1-methylindazol-5-yl)pyrazol-1-yl]-2-azaspiro[3.3]heptan-2-yl]prop-2-en-1-one Chemical compound ClC=1C(=C2C=NNC2=CC=1C)C=1C(=NN(C=1C)C1CC2(CN(C2)C(C=C)=O)C1)C=1C=C2C=NN(C2=CC=1)C AZUYLZMQTIKGSC-UHFFFAOYSA-N 0.000 description 12
- 238000009826 distribution Methods 0.000 description 11
- 229910052782 aluminium Inorganic materials 0.000 description 9
- 238000000137 annealing Methods 0.000 description 9
- 238000012360 testing method Methods 0.000 description 9
- 230000000670 limiting effect Effects 0.000 description 8
- 229910052791 calcium Inorganic materials 0.000 description 6
- 239000000203 mixture Substances 0.000 description 6
- 230000000704 physical effect Effects 0.000 description 6
- 229910045601 alloy Inorganic materials 0.000 description 5
- 239000000956 alloy Substances 0.000 description 5
- 230000008859 change Effects 0.000 description 5
- 238000000265 homogenisation Methods 0.000 description 5
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 4
- 238000011161 development Methods 0.000 description 4
- 238000010586 diagram Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 229910052748 manganese Inorganic materials 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- 230000002829 reductive effect Effects 0.000 description 4
- 238000004458 analytical method Methods 0.000 description 3
- 230000006866 deterioration Effects 0.000 description 3
- 238000003825 pressing Methods 0.000 description 3
- 229910052725 zinc Inorganic materials 0.000 description 3
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 2
- 229910000831 Steel Inorganic materials 0.000 description 2
- 238000009750 centrifugal casting Methods 0.000 description 2
- 238000004512 die casting Methods 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 230000008569 process Effects 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 238000011160 research Methods 0.000 description 2
- 238000007528 sand casting Methods 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- JBQYATWDVHIOAR-UHFFFAOYSA-N tellanylidenegermanium Chemical compound [Te]=[Ge] JBQYATWDVHIOAR-UHFFFAOYSA-N 0.000 description 2
- 229910018137 Al-Zn Inorganic materials 0.000 description 1
- 229910018573 Al—Zn Inorganic materials 0.000 description 1
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910002092 carbon dioxide Inorganic materials 0.000 description 1
- 239000001569 carbon dioxide Substances 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 239000003086 colorant Substances 0.000 description 1
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- 230000017525 heat dissipation Effects 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
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- 235000020985 whole grains Nutrition 0.000 description 1
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B3/003—Rolling non-ferrous metals immediately subsequent to continuous casting, i.e. in-line rolling
-
- 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 magnesium alloy sheet material and a method for producing the same. One embodiment of the present invention provides a magnesium alloy sheet material comprising, relative to 100% by weight of the entire magnesium alloy sheet material, 2.7 to 5.0% by weight of Al, 0.75 to 1.0% by weight of Zn, 0.1 to 1.0% by weight of Ca, 1.0% by weight or less (excluding 0% by weight) of Mn, and the balance Mg and other unavoidable impurities, wherein the volume fraction of basal plane grains is 30% or less relative to 100% by volume of the entire grains of the magnesium alloy sheet material, and the basal plane grains are grains oriented in the <0001 >/C axis direction.
Description
Technical Field
One embodiment of the present invention relates to a magnesium alloy sheet material and a method for manufacturing the same.
Background
Currently, the carbon dioxide emission limit of the international society and the importance of new renewable energy are becoming hot topics, and thus, a lightweight alloy, which is one of structural materials, is considered as a very attractive research field.
In particular, magnesium has a density of 1.74g/cm, as compared with other structural materials such as aluminum and steel
3The metal is the lightest metal, has various advantages such as vibration absorbing ability, electromagnetic wave shielding ability, and the like, and research on related industries aiming at utilizing the metal is actively being conducted.
Alloys containing such magnesium are now used not only in the field of electronic devices but also mainly in the automotive field, but have fundamental problems in corrosion resistance, flame resistance and formability, and have limitations in further expanding the range of applications.
In particular, magnesium has a HCP Structure (Hexagonal Closed Packed Structure) in relation to moldability, and a slip system at normal temperature is insufficient, which makes the processing difficult. That is, in the magnesium processing step, a large amount of heat is required, which directly leads to an increase in process cost.
On the other hand, among magnesium alloys, AZ-based alloys contain aluminum (Al) and zinc (Zn), and are relatively inexpensive while ensuring physical properties of appropriate strength and ductility to some extent, and are commercially available magnesium alloys.
However, the physical properties mentioned above merely mean an appropriate degree in magnesium alloys, and the strength is low compared with aluminum (Al) which is a competitive material.
Therefore, although it is necessary to improve physical properties such as low formability and strength of AZ-based magnesium alloys, studies on the properties have been far insufficient.
Disclosure of Invention
Provided are a magnesium alloy sheet material and a method for manufacturing the same.
Specifically, the center segregation of Al-Ca secondary phase grains is suppressed, and the formability of the magnesium plate is improved. Accordingly, it is an object to provide a magnesium alloy sheet material in which Al-Ca secondary phases are dispersed without being segregated to the center.
Moreover, the present inventors have also attempted to control the twinned structure by skin pass rolling, maintain formability, and improve strength. Specifically, skin pass rolling can minimize the change in the development of the (0001) texture, maintain moldability, and improve strength.
Means for solving the problems
The magnesium alloy sheet according to an embodiment of the present invention may provide a magnesium alloy sheet including, with respect to 100% by weight of the entire sheet, 2.7 to 5.0% by weight of Al, 0.75 to 1.0% by weight of Zn, 0.1 to 1.0% by weight of Ca, 1.0% by weight or less (excluding 0% by weight) of Mn, and the balance Mg and other unavoidable impurities, the volume fraction of basal plane grains being 30% or less with respect to 100% by volume of the crystal grains of the entire sheet, the basal plane grains being <0001>// C axis-oriented grains.
The magnesium alloy plate material may include Al — Ca secondary phase particles, and an area fraction difference between one quarter of the magnesium alloy plate material from the surface 1/4 and the Al — Ca secondary phase particles at a center of the magnesium alloy plate material from the surface 1/2 may be 10% or less.
Specifically, the ratio of the length of the center segregation may be less than 5% with respect to the entire length of the magnesium alloy sheet material in the rolling direction.
The thickness ratio of the center segregation may be less than 2.5% with respect to the entire thickness of the magnesium alloy sheet material in the thickness direction. Thus, the Al-Ca secondary phase particles of the magnesium alloy sheet material are not segregated in the center of the magnesium alloy sheet material, and can be uniformly distributed.
The Al — Ca secondary phase particles may contain, with respect to 100% by weight of the whole, 20.0 to 25.0% by weight of Al, 5.0 to 10.0% by weight of Ca, 0.1 to 0.5% by weight of Mn, 0.5 to 1.0% by weight of Zn, and the balance Mg and other unavoidable impurities.
The average particle diameter of the Al — Ca secondary phase particles may be 0.01 to 4 μm.
The Al-Ca secondary phase particles may be present per 100 μm of the area of the magnesium alloy sheet
2Contains 2to 15.
The Limit Dome Height (LDH) of the magnesium alloy sheet material may be 7mm or more.
The maximum collective strength may be 1to 4 with respect to the (0001) plane of the magnesium alloy sheet material.
The magnesium alloy sheet material may have a yield strength of 150 to 190 MPa.
A magnesium alloy sheet according to another embodiment of the present invention includes, with respect to 100 wt% of the total, 2.7 to 5.0 wt% of Al, 0.75 to 1.0 wt% of Zn, 0.1 to 1.0 wt% of Ca, 1.0 wt% or less (excluding 0 wt%) of Mn, and the balance Mg and other unavoidable impurities, and has an area fraction of a twinned structure of 35% or less with respect to 100 wt% of the total area of the magnesium alloy sheet.
Specifically, the area fraction of the twinned structure may be 5to 35% with respect to 100% of the total area of the magnesium alloy sheet material.
A magnesium alloy sheet material can be provided, wherein the volume fraction of basal plane grains is 30% or less relative to 100% by volume of the whole grains of the magnesium alloy sheet material, and the basal plane grains are grains oriented in the <0001>// C axis.
The limit vault height of the magnesium alloy sheet material can be more than 7 mm.
The maximum collective strength may be 1to 4 with respect to the (0001) plane of the magnesium alloy sheet material.
The magnesium alloy sheet material may have a yield strength of 200 to 300 MPa.
Effects of the invention
The magnesium alloy sheet material according to an embodiment of the present invention can disperse center segregation composed of Al — Ca secondary phase particles, and improve the formability of the magnesium sheet material. Accordingly, the magnesium alloy sheet material according to one embodiment of the present invention can provide a magnesium alloy sheet material in which the Al-Ca secondary phase is dispersed without being segregated at the center. Specifically, the difference in the area fraction of the Al — Ca secondary phase particles between the quarter portion from the surface 1/4 of the magnesium alloy plate material and the center portion from the surface 1/2 of the magnesium alloy plate material is 10% or less.
The magnesium alloy sheet according to another embodiment of the present invention can be produced by skin pass rolling, and the magnesium alloy sheet having a surface area ratio of a twinned structure of 35% or less is obtained with respect to 100% of the entire area of the magnesium alloy sheet. Specifically, the skin pass rolling step can minimize the development of the (0001) texture, control the twinned structure, and improve the strength while maintaining the formability.
Drawings
Fig. 1 is a schematic sequence diagram of a method for manufacturing a magnesium alloy sheet material according to an embodiment of the present invention.
FIG. 2 is an Optical microscope (Optical microscopy) photograph of a magnesium alloy sheet material produced in example 1 a.
FIG. 3 is an optical micrograph of a magnesium alloy sheet produced in comparative example 1 a.
FIG. 4 is a photograph taken by means of a Secondary electron microscope (Secondary Electron microscope) of the magnesium alloy plate produced in example 1 a.
FIG. 5 shows the results of measuring the limiting dome height (limiting dome height) of the magnesium alloy sheet manufactured in example 1 a.
FIG. 6 shows the integrated intensity of the maximum (0001) plane of example 1 a.
Fig. 7 shows the integrated intensity of the maximum (0001) plane of comparative example 1 a.
FIG. 8 shows the results of analyzing the magnesium alloy sheet manufactured in example 1a using EBSD (Electron Back scattering Diffraction).
FIG. 9 graphically shows the fractional crystallographic orientation of example 1 a.
FIG. 10 shows the results of analyzing a magnesium alloy plate using EBSD according to the skin pass rolling reduction.
Fig. 11 shows the maximum integrated intensity of the (0001) plane of example 2 and comparative example 2 according to the skin pass rolling conditions.
Detailed Description
The advantages and features of the invention and the methods of accomplishing the same will become apparent with reference to the following detailed description of the embodiments taken in conjunction with the accompanying drawings. However, the present invention is not limited to the embodiments disclosed below, and may be embodied in various forms different from each other, and these embodiments are provided only for making the disclosure of the present invention more complete, and to fully inform the scope of the present invention to those skilled in the art to which the present invention pertains, and the present invention is defined only by the scope of the claims. Like reference numerals refer to like elements throughout the specification.
Therefore, in several embodiments, well-known techniques are not specifically described in order to avoid obscuring the present invention. Unless defined otherwise, all terms (including technical and scientific terms) used in the present specification can be used as meanings commonly understood by one of ordinary skill in the art to which the present invention belongs. Throughout the specification, when a certain portion is referred to as including a certain structural element, unless specifically stated to the contrary, it means that other structural elements may be included, that is, other elements are not excluded. In addition, the singular forms also include the plural forms unless specifically stated in a sentence.
The magnesium alloy sheet material according to one embodiment of the present invention may contain, based on 100 wt% of the total magnesium alloy sheet material, 2.7 to 5.0 wt% of Al, 0.75 to 1.0 wt% of Zn, 0.1 to 1.0 wt% of Ca, 1.0 wt% or less of Mn (excluding 0 wt%), and the balance Mg and other unavoidable impurities.
The reasons for limiting the components and the composition will be explained below.
First, aluminum (Al) improves mechanical properties of the magnesium alloy sheet material, and improves castability of the melt. If Al is added in an amount of more than 5.0 wt%, a problem of sharp deterioration of castability may occur. If the Al content is less than 2.7 wt%, the mechanical properties of the magnesium alloy sheet material may deteriorate. Therefore, the content range of Al can be adjusted to the aforementioned range.
Zinc (Zn) improves the mechanical properties of the magnesium alloy sheet material. If the Zn addition is more than 1.0 wt%, a large amount of surface defects and center segregation are generated, which causes a problem of rapid deterioration of castability, and if the Zn addition is less than 0.75 wt%, a problem of deterioration of mechanical properties of the magnesium alloy sheet material occurs. Therefore, the content range of Zn can be adjusted to the aforementioned range.
Calcium (Ca) imparts flame resistance to the magnesium alloy sheet. If Ca is added in an amount of more than 1.0 wt%, the fluidity of the melt is reduced, the castability is deteriorated, the center segregation of the Al-Ca intermetallic compound is increased, and the formability of the magnesium alloy sheet material is deteriorated. If the amount of Ca added is less than 0.1% by weight, there is a problem that sufficient flame resistance cannot be imparted. Therefore, the content range of Ca can be adjusted to the aforementioned range. More specifically, Ca may be contained in 0.5 to 0.8 wt%.
Manganese (Mn) improves the mechanical properties of magnesium alloy sheets. If Mn is added in an amount of more than 1.0 wt%, the heat dissipation property is deteriorated and the uniform distribution control is difficult. Therefore, the content range of Mn can be adjusted to the aforementioned range.
The volume fraction of the basal plane crystal grains may be 30% or less with respect to 100% by volume of the entire crystal grains of the magnesium alloy sheet material.
In one embodiment of the present invention, by basal plane grains is meant grains having basal plane orientation. Specifically, magnesium has a hcp (hexagonal Closed pack) crystal structure, and in this case, a crystal grain when the C-axis of the crystal structure is a direction parallel to the thickness direction of the sheet is referred to as a crystal grain having an basal plane crystal orientation (i.e., basal plane crystal grain). Therefore, in the present specification, the basal plane grains may be identified as "< 0001>// C axis".
More specifically, when the fraction of the basal plane crystal grains is in the above range, a magnesium alloy sheet material having excellent formability can be obtained.
Specifically, the volume fraction of crystal grains having the <0001 >/C axis orientation relation may be 30% or less with respect to 100% by volume of the entire crystal grains of the magnesium alloy sheet material. More specifically, the volume fraction of crystal grains oriented in the <0001 >/C axis may be 25% or less based on 100% by volume of the whole crystal grains of the magnesium alloy sheet material. More specifically, it may be 20% or less. The lower limit of the volume fraction of the crystal grains having the <0001 >/C axis orientation relationship may exceed 0%. This means that any range in which the volume fraction of crystal grains having the orientation relationship of <0001>// C axis is present can be included in the present invention.
The magnesium alloy sheet material has an increased degree of orientation distribution of crystal grains, and the fraction of crystal grains oriented in the <0001>// C axis is decreased.
Therefore, when the range of the grain fraction of the <0001>// C axis orientation is satisfied, the bulk strength of the magnesium alloy sheet material is reduced, and a magnesium alloy sheet material having excellent formability can be obtained.
The magnesium alloy sheet material according to an embodiment of the present invention may include Al — Ca secondary phase particles.
Specifically, the magnesium alloy sheet material according to an embodiment of the present invention includes Al — Ca secondary phase particles, and may hardly include center segregation. More specifically, the magnesium alloy sheet according to an embodiment of the present invention may have a form in which the Al — Ca secondary phase particles are uniformly dispersed. The center segregation means that Al — Ca secondary phase particles are segregated in the center portion in the thickness direction (ND) of the magnesium alloy sheet material, and if the center segregation increases as described above, the formability of the magnesium alloy sheet material deteriorates.
Therefore, in the magnesium alloy sheet material according to one embodiment of the present invention, the difference in the area fraction of the Al — Ca secondary phase particles between the quarter portion from the surface 1/4 and the center portion from the surface 1/2 of the magnesium alloy sheet material may be 10% or less. Therefore, the Al-Ca secondary phase particles are not segregated in the center portion but uniformly dispersed as a whole, and the moldability can be improved. The term "area fraction" as used herein means the area fraction of Al-Ca secondary-phase particles per quarter and the center of the particle having the same area.
More specifically, the ratio of the length of the center segregation to the entire length of the magnesium alloy sheet material in the Rolling Direction (RD) is less than 5%. Further, the thickness ratio of the center segregation is less than 2.5% with respect to the entire thickness of the magnesium alloy sheet material in the thickness direction (ND).
The above description means that center segregation is hardly formed, and the length and thickness of segregation are reduced as compared with the center segregation generally generated by adding Al or Ca. Therefore, the magnesium alloy sheet material according to an embodiment of the present invention can improve formability.
The total length of the magnesium plate material may be based on a magnesium plate material having a predetermined length unit. Specifically, the length unit may be 1,000 to 3,000 μm.
Specifically, 20.0 to 25.0 wt% of Al, 5.0 to 10.0 wt% of Ca, 0.1 to 0.5 wt% of Mn, 0.5 to 1.0 wt% of Zn, and the balance Mg and other unavoidable impurities may be contained with respect to 100 wt% of the total of the Al — Ca secondary phase particles.
In general, when Al and Ca are added to magnesium to perform alloying, center segregation of Al — Ca secondary phase particles is generated, and formability is greatly lowered. On the contrary, the magnesium alloy sheet material according to one embodiment of the present invention can suppress the generation of center segregation composed of Al — Ca secondary phase particles, and improve the formability of the magnesium sheet material. Specifically, a magnesium alloy sheet material in which Al-Ca secondary phase particles are dispersed can be provided.
The average particle diameter of the Al-Ca secondary phase particles may be 0.01 to 4 μm. As the average particle diameter of the Al-Ca secondary phase particles becomes larger, the moldability becomes smaller due to the generation of center segregation as described above. At the particle diameter in the foregoing range, improved moldability is exhibited.
The Al-Ca secondary phase particles may be present in an amount of 100 μm per area of the magnesium alloy sheet
2Contains 2to 15. The formability of the magnesium alloy sheet can be improved by including Al-Ca secondary phase particles in the number within the above range.
In one embodiment of the present invention, in order to control the Al — Ca secondary phase grains, the composition ranges of Al, Zn, Mn, and Ca, the temperature and time conditions at the time of the homogenization heat treatment, the temperature and rolling reduction at the time of hot rolling, and the like can be precisely adjusted.
The magnesium alloy sheet material according to an embodiment of the present invention may include crystal grains, and the average particle diameter of the crystal grains may be 5to 30 μm. In the grain size range, moldability can be improved.
In addition, the limit dome height (limiting dome height) of the magnesium alloy sheet material according to the embodiment of the present invention may be 7mm or more. More specifically, it may be 7 to 10 mm.
In general, the limit dome height is used as an index for evaluating the formability (particularly, the compressibility) of a material, and an increase in the limit dome height means an increase in the formability of the material.
The limited range is due to an increased degree of orientation distribution of the crystal grains within the magnesium alloy sheet, which is a significantly higher limit dome height than the generally known magnesium alloy sheet.
Therefore, the magnesium alloy sheet material may have a maximum collective strength of 1to 4 with respect to the (0001) plane. If the amount exceeds the above range, the formability of the magnesium alloy sheet material may be deteriorated.
In addition, the magnesium alloy sheet according to an embodiment of the present invention may have a yield strength in the range of 150 to 190 MPa.
The magnesium alloy sheet according to one embodiment of the present invention may have a surface area fraction of a twinned structure of 35% or less with respect to 100% of the total area of the magnesium alloy sheet by skin pass rolling in the manufacturing step described later. More specifically, the area fraction of the double-textured structure may be 5to 35%. More specifically, the area fraction of the bimorph structure may be 5to 33%. By controlling the twinned structure fraction in the range, the yield strength of the magnesium alloy sheet material according to an embodiment of the present invention may be 200 to 300 MPa. This range is considered to be an excellent range in the magnesium plate material of the composition according to one embodiment of the present invention.
In addition, the thickness of the magnesium alloy sheet material according to an embodiment of the present invention may be 0.4 to 3 mm. The magnesium sheet material of one embodiment of the present invention may be selected according to the desired characteristics at the thickness range. However, the present invention is not limited to this thickness range.
Fig. 1 is a sequence diagram schematically showing a method for manufacturing a magnesium alloy sheet material according to an embodiment of the present invention. The sequence of the method for manufacturing the magnesium alloy sheet material of fig. 1 is only for illustrating the present invention, and the present invention is not limited thereto. Therefore, the method for manufacturing the magnesium alloy sheet material can be variously modified.
The method for manufacturing the magnesium alloy sheet material of one embodiment of the invention comprises the following steps: a step S10 of casting a melt containing, based on 100 wt% of the total, 2.7 to 5.0 wt% of Al, 0.75 to 1.0 wt% of Zn, 0.1 to 1.0 wt% of Ca, 1.0 wt% or less of Mn (excluding 0 wt%), and the balance Mg and other unavoidable impurities to produce a cast product; a step S20 of performing a homogenizing heat treatment on the cast product; and a step S30 of hot rolling the homogenized and heat treated cast product.
In addition, the manufacturing method of the magnesium alloy sheet material may further include other steps as necessary.
First, step S10 of producing a cast product by casting a melt containing, based on 100 wt% of the total, 2.7 to 5.0 wt% of Al, 0.75 to 1.0 wt% of Zn, 0.1 to 1.0 wt% of Ca, 1.0 wt% or less of Mn (excluding 0 wt%), and the balance Mg and other unavoidable impurities may be performed.
The reason for limiting the numerical values of the respective components is the same as described above, and therefore, the repetitive description thereof will be omitted.
In this case, the method S10 of manufacturing the cast product may be die casting, strip casting, billet casting, centrifugal casting, tilting casting, sand casting, Direct chill casting (Direct chill casting), or a combination thereof.
More specifically, a strip casting method may be used. However, the present invention is not limited thereto.
More specifically, in the step S10 of manufacturing the cast product, the reduction force may be 0.2ton/mm
2The above. More specifically, it may be 1ton/mm
2The above. More specifically, it may be 1to 1.5ton/mm
2. The cast member is subjected to a pressing force while being solidified, and at this time, the formability of the magnesium alloy sheet material can be improved by adjusting the pressing force to the above range.
Then, step S20 of performing a homogenizing heat treatment on the cast piece may be performed.
At this time, the heat treatment conditions may be heat treatment at a temperature of 350 ℃ to 500 ℃ for 1to 28 hours. More specifically, the homogenization heat treatment may be performed for 18 to 28 hours.
In the temperature range of less than 350 ℃, the homogenization heat treatment cannot be normally carried out, and the homogenization heat treatment may be carried outGenerating such as Mg
17Al
12The β phase (B) cannot be dissolved in the matrix.
In the temperature range of more than 500 c, the condensed β phase in the cast product melts to cause a fire or voids in the magnesium plate, and thus, the homogenization heat treatment can be performed in the aforementioned temperature range.
Then, the step S30 of hot rolling the homogenized and heat treated cast product may be performed.
At this time, the temperature condition of the hot rolling may be 150 to 350 ℃. In the temperature range below 150 ℃, the problem of multiple edge cracks occurs. In the temperature range higher than 500 ℃, a problem of unsuitability for mass production may occur. Therefore, hot rolling can be performed in the aforementioned temperature range.
The step of hot rolling may be performed a plurality of times, and hot rolling may be performed at a rolling rate of 10 to 30% at a time. The rolling reduction of the hot rolling means a value of% relative to 100% (length%) of the thickness of the cast product before hot rolling. By carrying out hot rolling several times, it is possible to finally roll to a thinner thickness of about 0.4 mm.
In the middle of the multiple hot rolling, the method can further comprise more than 1 intermediate annealing step. The formability of the magnesium alloy sheet can be further improved by including the intermediate annealing step. Specifically, the step of intermediate annealing may be performed at a temperature of 300 to 500 ℃ for a time of 1to 10 hours. More specifically, it may be carried out at a temperature of 450 to 500 ℃. Within the above range, the formability of the magnesium alloy sheet material can be further improved.
After the hot rolling step, a post heat treatment step may be further included. The formability of the magnesium alloy sheet material can be further improved by including a post heat treatment step. The post heat treatment step may be performed at 300 to 500 ℃ for a period of 1to 15 hours. Specifically, it may be carried out for a period of 1to 10 hours. Within the above range, the formability of the magnesium alloy sheet material can be further improved.
Still another method of manufacturing a magnesium alloy sheet material according to an embodiment of the present invention may include: a step of casting a melt containing 2.7 to 5.0 wt% of Al, 0.75 to 1.0 wt% of Zn, 0.1 to 1.0 wt% of Ca, 1.0 wt% or less of Mn (excluding 0 wt%), and the balance Mg and other unavoidable impurities, based on 100 wt% of the total, to produce a cast product; a step of subjecting the cast product to a homogenizing heat treatment; a step of hot rolling the homogenized and heat-treated cast product to produce a rolled product; a step of post-heat treating the rolled piece; and a step of producing a magnesium alloy plate by skin pass rolling the post-heat-treated rolled material.
First, a step of producing a cast product may be performed by using a melt containing, based on 100 wt% of the total, 2.7 to 5.0 wt% of Al, 0.75 to 1.0 wt% of Zn, 0.1 to 1.0 wt% of Ca, 1.0 wt% or less of Mn (excluding 0 wt%), and the balance Mg and other unavoidable impurities.
In the step, the melt may be commercial AZ31 alloy, AL5083 alloy, or a combination thereof. However, the present invention is not limited thereto.
More specifically, the melted liquid may be prepared at a temperature range of 650 to 750 ℃. Then, the melt may be cast to produce a cast article. At this time, the thickness of the casting may be 3 to 7 mm.
At this time, the method of manufacturing the cast product may utilize die casting, strip casting, billet casting, centrifugal casting, tilt casting, sand casting, Direct chill casting (Direct chill casting), or a combination thereof. More specifically, a strip casting method may be used. However, the present invention is not limited thereto.
More specifically, in the step of manufacturing the cast member, the reduction force may be 0.2ton/mm
2The above. More specifically, it may be 1ton/mm
2The above. More specifically, it may be 1to 1.5ton/mm
2。
Then, a step of homogenizing heat treatment of the cast may be performed.
More specifically, the step of subjecting the cast part to a homogenizing heat treatment may include: a first heat treatment step at a temperature range of 300 ℃ to 400 ℃; and a second heat treatment step at a temperature range of 400 ℃ to 500 ℃. The temperature ranges of the first heat treatment step and the second heat treatment step may be different.
More specifically, the first heat treatment step at a temperature range of 300 ℃ to 400 ℃ may be carried out for a time period of 5 hours to 20 hours. In addition, the second heat treatment step at a temperature ranging from 400 ℃ to 500 ℃ may be carried out for a time ranging from 5 hours to 20 hours.
By performing the first heat treatment step in the temperature range, the ternary system phase of Mg-Al-Zn occurring in the casting step can be eliminated. When the ternary system phase exists, it may adversely affect the subsequent processes. In addition, by carrying out the second heat treatment step in the temperature range, the stress in the slab can be released. Further, the formation of recrystallization of the cast structure can be more actively induced.
Then, a step of hot rolling the homogenized and heat treated cast product to produce a rolled product may be performed.
The heat treated cast part may be rolled to a thickness in the range of 0.4 to 3mm by 1to 15 rolling passes. In addition, the rolling may be performed at 150 to 350 ℃.
More specifically, when the rolling temperature is less than 150 ℃, cracks are induced in the surface during rolling, and when it exceeds 350 ℃, it is not suitable for actual mass production facilities. Thus, rolling may be performed at 150 ℃ to 350 ℃.
Then, a step of intermediate annealing the rolled material may be performed. When the rolling step is performed for a plurality of times, the heat treatment may be performed for a period of 1to 15 hours at a temperature range of 300 to 550 ℃ between one rolling and the next rolling.
For example, 2 passes of rolling may be followed by 1 pass of intermediate annealing to a final target thickness. For another example, the steel sheet may be rolled to a final target thickness by performing 1 annealing after 3 times of rolling. More specifically, when the rolled casting is annealed in the temperature range, the stress generated by the rolling can be released. Thus, multiple rolling passes can be made to achieve the desired cast thickness.
Then, a step of post-heat treating the rolled material may be performed.
The post heat treatment step may be carried out at 300 to 500 ℃ for a period of 1to 15 hours. Specifically, it may be carried out for a period of 1to 10 hours. Within the above range, the formability of the magnesium alloy sheet material can be further improved.
Finally, a step of skin pass rolling the post-heat-treated rolled material to manufacture a magnesium alloy sheet may be performed.
More specifically, skin pass rolling, also called temper rolling or temper rolling, means cold rolling at a relatively low pressure to remove a deformed pattern generated in a cold-rolled steel sheet after heat treatment and to increase hardness.
Thus, in one embodiment of the present invention, 1 skin pass rolling may be performed at a temperature ranging from 250 ℃ to 350 ℃.
The magnesium alloy sheet produced by skin pass rolling can be rolled at a rolling rate of 2to 15% with respect to the thickness of the rolled material. More specifically, the rolling rate may be linked to the skin pass temperature.
Specifically, for example, when the skin pass rolling temperature is 250 ℃, the skin pass rolling reduction may be 5to 15%. At this time, the yield strength may range from 200 to 260 MPa. At this time, the limit dome height may be in the range of 7.3 to 8.1.
Specifically, for example, when the skin pass rolling temperature is 300 ℃, the skin pass rolling reduction may be 5to 15%. More specifically, it may be 7 to 12%. At this time, the yield strength may range from 200 to 250 MPa. At this time, the limit dome height may be in the range of 7.3 to 8.1.
In the present application, the Limit Dome Height (LDH) is an index for evaluating the formability of a plate material, particularly the press formability, and is obtained by measuring the Height of deformation by applying deformation to a test piece and measuring the formability. When the limit crown height value is high, it may mean that the formability of the sheet material is excellent.
More specifically, when skin pass rolling is performed under the temperature and pressure conditions, the development of the (0001) integrated structure is reduced, and thus formability can be ensured. That is, when skin pass rolling is performed under the above-described conditions, the strength can be improved by minimizing the change in the strength of the integrated structure.
Hereinafter, the details will be described by examples. The following examples are merely illustrative of the present invention and the contents of the present invention are not limited to the following examples.
Example 1
A melt containing Al and Ca, 0.8 wt% Zn, 0.5 wt% Mn, and the balance Mg and inevitable impurities, as shown in table 1, in an amount of 100 wt% of the total, was prepared.
The molten metal is passed between two chill rolls to produce a magnesium casting. At this time, the pressing force of the chill roll is as shown in table 1 below.
The magnesium castings were then homogenized at 400 c for various times as shown in table 1 below.
The homogenized casting was hot rolled at a rolling reduction of 15% at a temperature of 250 ℃. Then, after an intermediate annealing was performed at the temperature disclosed in table 1 below for a period of 1 hour, the magnesium alloy sheet was hot-rolled at a temperature of 250 ℃ at a rolling reduction of 15%.
Comparative example 1
A melt containing Al and Ca, 0.8 wt% Zn, 0.5 wt% Mn, and the balance Mg and inevitable impurities, as shown in table 1, in an amount of 100 wt% of the total, was prepared.
A magnesium alloy sheet was manufactured in the same manner as in example 1, except for the conditions disclosed in table 1 below.
[ TABLE 1 ]
The following experimental examples were carried out in order to compare and evaluate the physical properties of the examples and comparative examples produced above.
Experimental example 1: microscopic Structure Observation of magnesium alloy sheet Material
The microstructure of the magnesium alloy plate materials produced in examples and comparative examples was observed by a Scanning Electron Microscope (SEM).
This is disclosed in fig. 2to 4 of the present application.
FIG. 2 is a Scanning Electron Microscope (SEM) photograph of the magnesium alloy sheet material produced in example 1 a. FIG. 3 is a SEM photograph of a magnesium alloy sheet material produced in comparative example 1 a.
Specifically, the horizontal direction in fig. 2to 3 means the Rolling Direction (RD) of the magnesium alloy sheet material, and the vertical direction means the thickness direction (ND).
As shown in fig. 2, it is understood that in example 1a, center segregation hardly occurs in the magnesium alloy sheet material. Specifically, it was found that the ratio of the center segregation length was less than 5% with respect to the total length in the rolling direction of example 1a, which was about 2000 μm.
On the contrary, as shown in fig. 3, it is understood that in comparative example 1a, the center segregation is generated in a large amount. Specifically, it is found that the center segregation length ratio of comparative example 1a, which is about 2000 μm in the entire length in the rolling direction, is 5% or more. In addition, it was confirmed that in comparative example 1a, the thickness of center segregation was about 30 μm with respect to the total thickness of about 1200 μm in the thickness direction. Therefore, it is found that the thickness ratio of the center segregation with respect to the entire thickness in the thickness direction of the magnesium alloy sheet material is 2.5%. Therefore, it was confirmed that the center segregation occurred in a large amount in comparative example 1 a.
Therefore, the center segregation is a factor of lowering the formability of the magnesium alloy sheet material, and therefore, the less the center segregation is generated, the more excellent the formability of the magnesium alloy sheet material can be obtained.
FIG. 4 is a photograph taken by means of a Secondary electron microscope (Secondary Electron microscope) of the magnesium alloy plate produced in example 1 a.
The white dots in FIG. 4 mean Al-Ca secondary phase particles. More specifically, the white portion in fig. 4 was analyzed for 24.61 wt% of Al, 8.75 wt% of Ca, 0.36 wt% of Mn, 0.66 wt% of Zn, and the balance Mg and other unavoidable impurities as a result of the composition analysis.
From this, it was confirmed that the magnesium alloy sheet material of example 1a contained Al-Ca secondary phase particles. Specifically, it can be seen that the area of the magnesium alloy plate material in FIG. 4 is 1600 μm per one area
2The distribution of Al-Ca secondary phase particles is 50.
However, as disclosed in FIG. 4, it is clear that in example 1a, the Al-Ca secondary phase is dispersed without being segregated. Thus, as disclosed in the following Table 2, it can be seen that the limited dome height of the example 1a of the present application is 9.4mm, whereas the limited dome height of the comparative example 1a is 2.5mm, which is inferior in moldability to the examples.
Experimental example 2: limit dome height measurement of magnesium alloy sheet
In the present application, the Limit Dome Height (LDH) is an index for evaluating the formability, particularly the press formability of a sheet material, and the formability is measured by applying a strain to a test piece and measuring the Height of the strain.
The magnesium alloy sheet materials of examples and comparative examples were inserted between an upper die and a lower die, the outer peripheral portions of the test pieces were fixed by a force of 5kN, and a known press oil was used as the lubricating oil. Further, it was performed in such a manner that deformation was applied at a speed of 5to 10mm/min using a spherical punch having a diameter of 20mm, the punch was inserted until each test piece was broken, and then the deformation height of each test piece at the time of breakage was measured. I.e. the height of deformation of the test piece.
This is disclosed in the present application in fig. 5.
FIG. 5 shows the results of measuring the limiting dome height (limiting dome height) of the magnesium alloy sheet manufactured in example 1 a.
As disclosed in fig. 5, the magnesium alloy sheet material of example 1a was excellent in formability.
This can be confirmed in tables 2 and 3 below.
Experimental example 3: crystallographic orientation analysis of crystal grains
The crystal orientations of the crystal grains of the magnesium alloy sheet materials of the examples and comparative examples were confirmed by an XRD analyzer and are shown in fig. 6 to 11. Specifically, the XRD polar pattern (Pole Figure) method showed an aggregate structure of crystal grains.
More specifically, the polar diagram is displayed by stereoscopically projecting the direction of an arbitrarily fixed crystal coordinate system on the test piece coordinate system. More specifically, the pole of the {0001} plane with respect to the crystal grains of various orientations is displayed in a reference coordinate system, and density contours are drawn in accordance with the pole density distribution, whereby a pole figure can be displayed. In this case, the poles are fixed in a specific grid direction by bragg angles, and a plurality of poles can be displayed for a single crystal.
Therefore, it can be explained that the smaller the density distribution value of the contour line shown in the polar diagram method, the more oriented crystal grains are distributed, and the larger the density distribution value, the more oriented crystal grains are distributed in the <0001>// C axis.
This can be compared with fig. 6 and 7 of the present application.
Fig. 6 shows the maximum integrated intensity of the (0001) plane of example 1 a. Fig. 7 shows the maximum integrated intensity of the (0001) plane of comparative example 1 a.
Specifically, the maximum integrated intensity of the (0001) plane in fig. 6 and 7 is a result of analyzing the crystal orientation of the magnesium alloy sheet material with the XRD analyzer.
As disclosed in fig. 6, it was confirmed that the maximum density distribution value (integrated intensity) of the (0001) plane was 2.73 in the example, whereas 12.1 in the comparative example was higher than that in the example.
That is, the maximum integrated intensity values of the examples were small, the contour lines were widely dispersed, and the grain distribution of various orientations was derived.
In contrast, the maximum integrated intensity values of the comparative examples were large, and the contour lines were dense, and thus it was found that the comparative examples contained a larger amount of crystal grains having <0001>// C-axis orientation than the examples.
This indicates that the examples are more excellent in moldability.
This is also apparent from fig. 8 and 9 of the present application.
FIG. 8 shows the results of analyzing the magnesium alloy sheet manufactured in example 1a using EBSD (Electron Back scattering Diffraction).
FIG. 9 graphically shows the fractional crystallographic orientation of example 1 a.
First, as disclosed in fig. 8, even with EBSD, the crystal orientation of the crystal grains can be measured. More specifically, EBSD can measure the crystal orientation of crystal grains by inelastic scattering diffraction at the back of a test piece by injecting electrons into the test piece by an e-beam.
As disclosed in fig. 9, a crystal grain having a misorientation angle (misorientation angle) of 20 ° or less may be referred to as a basal plane crystal grain. Therefore, it was confirmed that the volume fraction distribution of <0001>// C-axis oriented crystal grains was about 18.5% distribution with respect to 100% of the volume fraction of the whole crystal grains.
Further, as disclosed in FIG. 8, it was found that crystal grains having various orientations were distributed in various colors, and the EBSD result revealed that crystal grains (red) corresponding to crystal grains having <0001>// C-axis orientation could be visually confirmed
[ TABLE 2 ]
As a result, it was confirmed that the moldability was inferior to that of examples in comparative examples 1a to 1d which could not satisfy the conditions of the homogenizing annealing time, the rolling temperature and the intermediate annealing temperature. Furthermore, it is found that the yield strength is inferior to that of the examples. In comparative example 1c, the average size of crystal grains was about 40 μm, and the moldability was relatively excellent compared with other comparative examples, but the level was not as good as that of the examples.
Example 2
A melt containing 3.0 wt% of Al, 1.0 wt% of Zn, 1.0 wt% of Ca, 0.3 wt% of Mn, and the balance Mg and other unavoidable impurities with respect to 100 wt% of the total was prepared.
Casting the melt to produce a cast part.
The casting was subjected to a first homogenizing heat treatment at 350 ℃ for 10 hours. The cast product of the first homogenizing heat treatment was subjected to a second homogenizing heat treatment at 450 ℃ for a period of 10 hours.
Rolling the homogenized and heat-treated cast product to produce a rolled product.
Thereafter, the rolled piece was post-heat treated at 400 ℃ for 10 hours.
Finally, skin pass rolling was performed on the post-heat-treated rolled material to produce a magnesium plate, and the skin pass rolling temperature and the rolling reduction were as shown in table 2.
Comparative example 2
A magnesium alloy plate was produced in the same manner as in example 2, except for the skin pass rolling temperature and the rolling reduction conditions.
In order to compare and evaluate the physical properties of the examples and comparative examples, the following experimental examples were carried out. In addition, the experimental examples also carried out the measurement of the height of the limiting dome and the analysis of the crystallographic orientation, the test methods being the same as those described above.
Experimental example 4: comparison of physical Properties at different skin pass Rolling reduction ratios and temperatures
[ TABLE 3 ]
As disclosed in table 3, the magnesium alloys having the same composition and composition were subjected to skin pass rolling, and as a result, the formability was not significantly changed, and the yield strength was improved. More specifically, the formability can be compared with the values of the elongation and the limit dome height.
Also, this minimizes the variation of the texture of the set, so that formability can be ensured, and the variation of the texture at different skin pass rolling reduction ratios can be confirmed by fig. 10.
FIG. 10 shows the results of analyzing a magnesium alloy plate using EBSD according to the skin pass rolling reduction.
As disclosed in fig. 10, even when skin pass rolling is performed after rolling, the grain distribution of various orientations can be confirmed. Further, when the skin pass rolling is performed at a high skin pass rolling reduction ratio, the change in orientation of the texture is minimized by the development of the twinned (black) texture and dislocations, and the strength can be increased.
Specifically, when the skin pass rolling reduction was 2to 6%, the area fraction of the twinned structure was confirmed to be 15% with respect to 100% of the total area. When the skin pass rolling reduction was 6 to 15%, the area fraction of the twinned structure was confirmed to be 30% with respect to 100% of the total area.
As described above, the strength of the magnesium alloy sheet material can be maintained and the formability can be improved due to the twinned structure and dislocations.
Therefore, in the case of rolling at a reduction ratio exceeding 15% (comparative example 2a), the texture of the (0001) plane again progresses, and the formability is deteriorated.
Fig. 11 shows the maximum integrated intensity of the (0001) plane of example 2 and comparative example 2 according to the skin pass rolling conditions.
As disclosed in fig. 11, it is understood that the change of the texture of the example is not large even when skin pass rolling is performed. However, as shown in comparative example 2a, it is found that the strength of the texture greatly changes when the skin pass rolling reduction is excessive. Therefore, as disclosed in table 3, it was confirmed that comparative example 2a has an excellent effect of increasing the yield strength but a very poor elongation.
Further, it was confirmed that the effect of increasing the yield strength at different skin pass rolling reduction ratios was greater than the effect of increasing the yield strength at a change in skin pass rolling temperature.
Although the embodiments of the present invention have been described above with reference to the drawings, those skilled in the art to which the present invention pertains will appreciate that the present invention can be embodied in other specific forms without changing the technical spirit or essential features of the present invention.
It is therefore to be understood that the above-described embodiments are illustrative in all respects, and not restrictive. The scope of the present invention is indicated by the appended claims, rather than the detailed description, and all changes and modifications that come within the meaning and range of equivalency of the claims are to be construed as being embraced therein.
Claims (10)
1. A magnesium alloy sheet material, wherein,
comprising 2.7 to 5.0 wt% of Al, 0.75 to 1.0 wt% of Zn, 0.1 to 1.0 wt% of Ca, 1.0 wt% or less of Mn except 0 wt%, and the balance of Mg and other unavoidable impurities, based on 100 wt% of the total magnesium alloy sheet material,
the volume fraction of the basal plane crystal grains is 30% or less based on 100% by volume of the whole crystal grains of the magnesium alloy plate material,
the basal plane crystal grains are crystal grains with <0001 >/C axis orientation.
2. The magnesium alloy sheet according to claim 1,
the magnesium alloy sheet material contains Al-Ca secondary phase particles, and
the difference in the area fraction of Al-Ca secondary phase particles between a quarter of the distance from the surface 1/4 of the magnesium alloy plate material and the center of the distance from the surface 1/2 of the magnesium alloy plate material is 10% or less.
3. The magnesium alloy sheet according to claim 2,
the ratio of the length of the center segregation to the entire length of the magnesium alloy sheet material in the rolling direction is less than 5%.
4. The magnesium alloy sheet according to claim 3,
the thickness ratio of the center segregation is less than 2.5% with respect to the entire thickness of the magnesium alloy sheet material in the thickness direction.
5. The magnesium alloy sheet according to claim 4,
the limit vault height (LDH) of the magnesium alloy sheet material is more than 7mm,
the maximum collective strength is 1to 4 on the basis of the (0001) plane of the magnesium alloy sheet.
6. A magnesium alloy sheet material, wherein,
comprising 2.7 to 5.0 wt% of Al, 0.75 to 1.0 wt% of Zn, 0.1 to 1.0 wt% of Ca, 1.0 wt% or less, and Mn except 0 wt%, the balance of Mg and other unavoidable impurities based on 100 wt% of the total magnesium alloy sheet material,
the surface area ratio of the twinned structure is 35% or less with respect to 100% of the total area of the magnesium alloy sheet material.
7. The magnesium alloy sheet according to claim 6,
the area fraction of the twinned structure is 5to 35% relative to 100% of the total area of the magnesium alloy sheet material.
8. The magnesium alloy sheet according to claim 7,
the volume fraction of the basal plane crystal grains is 30% or less based on 100% by volume of the whole crystal grains of the magnesium alloy plate material,
the basal plane crystal grains are crystal grains with <0001 >/C axis orientation.
9. The magnesium alloy sheet according to claim 8,
the limit vault height of the magnesium alloy sheet is more than 7mm,
the maximum collective strength is 1to 4 on the basis of the (0001) plane of the magnesium alloy sheet.
10. The magnesium alloy sheet according to claim 9,
the yield strength of the magnesium alloy sheet is 200 to 300 MPa.
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| KR10-2017-0079982 | 2017-06-23 | ||
| KR1020170079982A KR20190000676A (en) | 2017-06-23 | 2017-06-23 | Magnesium alloy sheet and manufacturing for the same |
| PCT/KR2018/007030 WO2018236163A1 (en) | 2017-06-23 | 2018-06-21 | Magnesium alloy sheet and manufacturing method therefor |
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| US (1) | US20210147964A1 (en) |
| EP (1) | EP3643802A4 (en) |
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| KR20090120194A (en) * | 2008-05-19 | 2009-11-24 | 포항공과대학교 산학협력단 | Magnesium alloy panel having high strength and manufacturing method for the same |
| JP2010229467A (en) * | 2009-03-26 | 2010-10-14 | Hitachi Metals Ltd | Method of producing magnesium alloy thin plate |
| JP2011179075A (en) * | 2010-03-01 | 2011-09-15 | National Institute Of Advanced Industrial Science & Technology | Magnesium alloy sheet material having improved cold-formability and in-plane anisotropy, and method for manufacturing the same |
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| CN108472699A (en) * | 2015-12-23 | 2018-08-31 | 株式会社Posco | Magnesium alloy plate and its manufacturing method |
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| JP2011127163A (en) * | 2009-12-16 | 2011-06-30 | Mitsubishi Alum Co Ltd | Magnesium alloy sheet material having excellent formability, and method for production thereof |
| JP5660525B2 (en) * | 2010-03-05 | 2015-01-28 | 独立行政法人産業技術総合研究所 | General-purpose magnesium alloy sheet that exhibits formability similar to that of aluminum alloy and method for producing the same |
| JP2012077320A (en) * | 2010-09-30 | 2012-04-19 | Mitsubishi Alum Co Ltd | Magnesium alloy sheet material for bending and method for producing the same, and magnesium alloy pipe and method for producing the same |
| KR101751521B1 (en) * | 2015-12-24 | 2017-06-27 | 주식회사 포스코 | Method of manufacturing magnesium alloy sheet |
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- 2017-06-23 KR KR1020170079982A patent/KR20190000676A/en not_active Application Discontinuation
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- 2018-06-21 JP JP2019570977A patent/JP2020524219A/en active Pending
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- 2018-06-21 WO PCT/KR2018/007030 patent/WO2018236163A1/en unknown
- 2018-06-21 EP EP18820051.3A patent/EP3643802A4/en not_active Withdrawn
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| Publication number | Priority date | Publication date | Assignee | Title |
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| KR20090120194A (en) * | 2008-05-19 | 2009-11-24 | 포항공과대학교 산학협력단 | Magnesium alloy panel having high strength and manufacturing method for the same |
| JP2010229467A (en) * | 2009-03-26 | 2010-10-14 | Hitachi Metals Ltd | Method of producing magnesium alloy thin plate |
| JP2011179075A (en) * | 2010-03-01 | 2011-09-15 | National Institute Of Advanced Industrial Science & Technology | Magnesium alloy sheet material having improved cold-formability and in-plane anisotropy, and method for manufacturing the same |
| KR101481909B1 (en) * | 2013-08-08 | 2015-01-13 | 주식회사 포스코 | Manufacturing method of magnesium alloy |
| KR20150065418A (en) * | 2013-12-05 | 2015-06-15 | 주식회사 포스코 | magnesium-alloy plate and manufacturing method of it |
| CN108472699A (en) * | 2015-12-23 | 2018-08-31 | 株式会社Posco | Magnesium alloy plate and its manufacturing method |
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| US20210147964A1 (en) | 2021-05-20 |
| KR20190000676A (en) | 2019-01-03 |
| EP3643802A4 (en) | 2020-07-29 |
| JP2020524219A (en) | 2020-08-13 |
| WO2018236163A1 (en) | 2018-12-27 |
| EP3643802A1 (en) | 2020-04-29 |
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