EP3643802A1 - Blech aus einer magnesiumlegierung und herstellungsverfahren dafür - Google Patents

Blech aus einer magnesiumlegierung und herstellungsverfahren dafür Download PDF

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Publication number
EP3643802A1
EP3643802A1 EP18820051.3A EP18820051A EP3643802A1 EP 3643802 A1 EP3643802 A1 EP 3643802A1 EP 18820051 A EP18820051 A EP 18820051A EP 3643802 A1 EP3643802 A1 EP 3643802A1
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EP
European Patent Office
Prior art keywords
magnesium alloy
alloy sheet
crystal grains
less
rolling
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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Application number
EP18820051.3A
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English (en)
French (fr)
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EP3643802A4 (de
Inventor
Jun Ho Park
Oh-Duck Kwon
Sang Hyun Kim
Jae Joong Kim
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Posco Holdings Inc
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Posco Co Ltd
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Application filed by Posco Co Ltd filed Critical Posco Co Ltd
Publication of EP3643802A1 publication Critical patent/EP3643802A1/de
Publication of EP3643802A4 publication Critical patent/EP3643802A4/de
Withdrawn legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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

Definitions

  • An embodiment of the present invention relates to a magnesium alloy sheet and a manufacturing method therefor.
  • magnesium is the lightest metal with a density of 1.74 g/cm 3 and has various advantages such as vibration absorbing ability and electromagnetic wave shielding ability as compared with other structural materials such as aluminum and steel. Therefore, research of related industry has been actively carried out to utilize magnesium.
  • An alloy containing magnesium has been currently applied not only in the field of electronic device but also in the field of vehicle, but it has fundamental problems in corrosion resistance, flame resistance, and formability, and thus there are limitations in expanding the application range thereof.
  • magnesium has a hexagonal closed packed (HCP) structure, such that a slip system is not enough at room temperature, which makes it difficult to perform a processing process thereof. That is, a large amount of heat is required in a processing process of magnesium, which leads to an increase in the cost of the processing process.
  • HCP hexagonal closed packed
  • an AZ-based alloy contains aluminum (Al) and zinc (Zn), and corresponds to a commercialized magnesium alloy, because it is inexpensive while securing physical properties of a somewhat appropriate strength and ductile.
  • the strength of the AZ-based alloy is lower than that of aluminum (Al) which is a competitive material.
  • the present invention has been made in an effort to provide a magnesium alloy sheet and a manufacturing method therefor.
  • the present invention is to improve formability of a magnesium sheet by suppressing center segregation consisting of Al-Ca secondary phase particles. Accordingly, the present invention is to provide a magnesium alloy sheet in which Al-Ca secondary phases are dispersed without being segregated in the center of the magnesium alloy sheet.
  • the present invention is to improve a strength of a magnesium alloy sheet by controlling a twinned crystal structure through skin pass rolling while maintaining the formability of the magnesium alloy sheet.
  • a strength of a magnesium alloy sheet may be increased while maintaining formability of the magnesium alloy sheet by minimizing a development change in texture of (0001) through skin pass rolling.
  • An exemplary embodiment of the present invention provides a magnesium alloy sheet containing, relative to 100 wt% of the entire magnesium alloy sheet, 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 of Mg and other inevitable impurities, wherein a volume fraction of bottom crystal grains, relative to 100 vol% of overall crystal grains of the magnesium alloy sheet, is 30% or less, and the bottom crystal grains are crystal grains in a ⁇ 0001>//C-axis direction.
  • the magnesium alloy sheet may include Al-Ca secondary phase particles, and a difference in area fraction of the Al-Ca secondary phase particles between a quarter portion (1/4) of a surface of the magnesium alloy sheet and a center portion (1/2) of the surface of the magnesium alloy sheet may be 10% or less.
  • a ratio of a length of center segregation to a total length of the magnesium alloy sheet in a rolling direction may be less than 5%.
  • a ratio of a thickness of the center segregation to a total thickness of the magnesium alloy sheet in a thickness direction may be less than 2.5%. Therefore, in the magnesium alloy sheet, the Al-Ca secondary phase particles may be uniformly distributed without being segregated in the center portion of the magnesium alloy sheet.
  • the Al-Ca secondary phase particle may contain, relative to 100 wt% of the entire Al-Ca secondary phase particle, 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 of Mg and other inevitable impurities.
  • An average particle size of the Al-Ca secondary phase particles may be 0.01 to 4 ⁇ m.
  • Al-Ca secondary phase particles may be included per area of 100 ⁇ m 2 of the magnesium alloy sheet.
  • a limiting dome height (LDH) of the magnesium alloy sheet may be 7 mm or more.
  • a maximum texture intensity of a (0001) surface of the magnesium alloy sheet may be 1 to 4.
  • a yield strength of the magnesium alloy sheet may be 150 to 190 MPa.
  • Another exemplary embodiment of the present invention provides a magnesium alloy sheet containing: relative to 100 wt% of the entire magnesium alloy sheet, 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 of Mg and other inevitable impurities, wherein a volume fraction of a twinned crystal structure, relative to 100 vol% of the entire area of the magnesium alloy sheet, is 35% or less.
  • the volume fraction of the twinned crystal structure, relative to 100 vol% of the entire area of the magnesium alloy sheet, may be 5 to 35%.
  • the magnesium alloy sheet in which a volume fraction of bottom crystal grains, relative to 100 vol% of overall crystal grains of the magnesium alloy sheet, is 30% or less, and the bottom crystal grains are crystal grains in a ⁇ 0001 >//C-axis direction may be provided.
  • a limiting dome height of the magnesium alloy sheet may be 7 mm or more.
  • a maximum texture intensity of a (0001) surface of the magnesium alloy sheet may be 1 to 4.
  • a yield strength of the magnesium alloy sheet may be 200 to 300 MPa.
  • the center segregations consisting of Al-Ca secondary phase particles are dispersed, such that the formability the magnesium sheet may be improved. Accordingly, according to an embodiment of the present invention, it is possible to provide the magnesium alloy sheet in which the Al-Ca secondary phases are dispersed without being segregated in the center of the magnesium alloy sheet. Specifically, it is possible to provide the magnesium alloy sheet in which a difference in area fraction of the Al-Ca secondary phase particles between a quarter portion (1/4) of a surface of the magnesium alloy sheet and a center portion (1/2) of the surface of the magnesium alloy sheet is 10% or less.
  • the magnesium alloy sheet in which an area fraction of a twinned crystal structure, relative to 100% of the entire area of the magnesium alloy sheet, is 35% or less.
  • the strength of the magnesium alloy sheet may be improved by controlling the twinned crystal structure while maintaining the formability of the magnesium alloy sheet by minimizing the development of a texture of (0001) through a skin pass process.
  • a magnesium alloy sheet according to an embodiment of the present invention may contain, relative to 100 wt% of the entire magnesium alloy sheet, 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 of Mg and other inevitable impurities.
  • Al improves the mechanical properties of the magnesium alloy sheet and castability of a molten metal.
  • Al is added in an amount of more than 5.0 wt%, the castability may rapidly deteriorate.
  • Al is added in an amount of less than 2.7 wt%, the mechanical properties of the magnesium alloy sheet may deteriorate. Therefore, a content of Al may be adjusted within the above-mentioned range.
  • Zinc (Zn) improves the mechanical properties of the magnesium alloy sheet.
  • Zn Zinc
  • a content of Zn may be adjusted within the above-mentioned range.
  • Calcium (Ca) imparts flame resistance to the magnesium alloy sheet.
  • Ca When Ca is added in an amount of more than 1.0 wt%, the castability may rapidly deteriorate due to reduction of fluidity of the molten metal, and the formability of the magnesium alloy sheet may deteriorate due to an increase of the center segregation consisting of an Al-Ca-based intermetallic compound.
  • Ca When Ca is added in an amount of less than 0.1 wt%, the flame resistance may not be sufficiently imparted. Therefore, a content of Ca may be adjusted within the above-mentioned range. More specifically, Ca may be contained in an amount of 0.5 to 0.8 wt%.
  • Manganese (Mn) improves the mechanical properties of the magnesium alloy sheet.
  • Mn is added in an amount of more than 1.0 wt%, a heat dissipation property may deteriorate and uniform distribution control may be difficult. Therefore, a content of Mn may be adjusted within the above-mentioned range.
  • the volume fraction of bottom crystal grains, relative to 100 vol% of overall crystal grains of the magnesium alloy sheet may be 30% or less.
  • a bottom crystal grain refers to a crystal grain with a bottom orientation.
  • magnesium has a hexagonal closed pack (HCP) crystal structure, here, a crystal grain when a C-axis of the crystal structure is parallel to a thickness direction of the sheet refers to a crystal grain with a bottom crystal orientation (that is, bottom crystal grain).
  • HCP hexagonal closed pack
  • the bottom crystal grain may be expressed as a " ⁇ 0001>//C-axis”.
  • a magnesium alloy sheet having an excellent formability may be obtained.
  • the volume fraction of bottom crystal grains in the ⁇ 0001>//C-axis direction, relative to 100 vol% of overall crystal grains of the magnesium alloy sheet may be 30% or less. More specifically, the volume fraction of bottom crystal grains in the ⁇ 0001>HC-axis direction, relative to 100 vol% of overall crystal grains of the magnesium alloy sheet may be 25% or less. Still more specifically, the volume fraction of bottom crystal grains in the ⁇ 0001>//C-axis direction, relative to 100 vol% of overall crystal grains of the magnesium alloy sheet may be 20% or less.
  • a lower limit of the volume fraction of bottom crystal grains in the ⁇ 0001>//C-axis may be more than 0%. This means that in a case where the volume fraction of crystal grains in the ⁇ 0001>//C-axis direction is in any range (more than 0%), the magnesium alloy sheet may be included in the present invention.
  • the fraction of crystal grains in the ⁇ 0001 >//C-axis direction may be decreased due to an increase of the orientation distribution of crystal grains.
  • the texture intensity of the magnesium alloy sheet is decreased, such that a magnesium alloy sheet having an excellent formability may be obtained.
  • the magnesium alloy sheet according to an embodiment of the present invention may include Al-Ca secondary phase particles.
  • the magnesium alloy sheet according to an embodiment of the present invention may include the Al-Ca secondary phase particles, but may hardly include the 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 refers to that Al-Ca secondary phase particles are segregated in the center portion of the magnesium alloy sheet in the thickness direction (ND), and as described above, as the center segregation increases, the formability of the magnesium alloy sheet may deteriorate.
  • a difference in area fraction of the Al-Ca secondary phase particles between a quarter portion (1/4) of a surface of the magnesium alloy sheet and the center portion (1/2) of the surface of the magnesium alloy sheet may be 10% or less. Therefore, the Al-Ca secondary phase particles are entirely and uniformly dispersed without segregation in the center portion of the magnesium alloy sheet, and the formability of the magnesium alloy sheet may thus be improved.
  • the area fraction refers to a fraction with respect to an area of the Al-Ca secondary phase particles per same area of the quarter portion and the center portion.
  • a ratio of a length of the center segregation to the total length of the magnesium alloy sheet in the rolling direction (RD) may be less than 5%.
  • a ratio of a thickness of the center segregation to the total thickness of the magnesium alloy sheet in the thickness direction (ND) may be less than 2.5%.
  • the above description means that the center segregation is hardly generated, and the above range is a range in which both the length and thickness of the center segregation are decreased as compared to center segregation which is generally generated when Al and Ca are added. Therefore, the formability of the magnesium alloy sheet according to an embodiment of the present invention may be improved.
  • the total length of the magnesium sheet may be based on a magnesium sheet with a constant length unit. Specifically, the length unit may be 1,000 to 3,000 ⁇ m.
  • the Al-Ca secondary phase particle may contain, relative to 100 wt% of the entire Al-Ca secondary phase particle, 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 of Mg and other inevitable impurities.
  • the magnesium alloy sheet according to an embodiment of the present invention may improve the formability of the magnesium sheet by suppressing the generation of the center segregation consisting of Al-Ca secondary phase particles.
  • the magnesium alloy sheet in which Al-Ca secondary phase particles are dispersed may be provided.
  • An average particle size of the Al-Ca secondary phase particles may be 0.01 to 4 ⁇ m. As the average particle size of the Al-Ca secondary phase particles is large, as described above, the formability of the magnesium alloy sheet may deteriorate due to the generation of the center segregation. Within the above-mentioned range of the particle size, the improved formability may be exhibited.
  • Al-Ca secondary phase particles may be included per area of 100 ⁇ m 2 of the magnesium alloy sheet.
  • the number of Al-Ca secondary phase particles is in the above-mentioned range, the formability of the magnesium alloy sheet may be improved.
  • composition ranges of Al, Zn, Mn, and Ca in order to control the Al-Ca secondary phase particles, composition ranges of Al, Zn, Mn, and Ca, temperature and time conditions during homogenization heat treatment, temperature and rolling ratio during warm-rolling, and the like may be precisely controlled.
  • the magnesium alloy sheet according to an embodiment of the present invention includes crystal grains, and an average particle size of the crystal grains may be 5 to 30 ⁇ m. Within the above particle size range of the crystal grains, the formability of the magnesium alloy sheet may be improved.
  • a limiting dome height of the magnesium alloy sheet according to an embodiment of the present invention may be 7 mm or more. More preferably, the limiting dome height of the magnesium alloy sheet may be 7 to 10 mm.
  • a limiting dome height is utilized as an index for evaluating formability (in particular, pressability) of a material, and as the limiting dome height is increased, the formability of the material is improved.
  • a limiting dome height within the above limited range is a significantly higher limiting dome height than that of a magnesium alloy sheet generally known, which caused by an increase in orientation distribution of the crystal grain in the magnesium alloy sheet.
  • the maximum texture intensity of a (0001) surface of the magnesium alloy sheet may be 1 to 4.
  • the formability of the magnesium alloy sheet may deteriorate.
  • a yield strength of the magnesium alloy sheet according to an embodiment of the present invention may be in a range of 150 to 190 MPa.
  • an area fraction of a twinned crystal structure may be 35% or less relative to 100% of the entire area of the magnesium alloy sheet. More specifically, the area fraction of the twinned crystal structure may be 5 to 35%. Still more specifically, the area fraction of the twinned crystal structure may be 5 to 33%.
  • the yield strength of the magnesium alloy sheet according to an embodiment of the present invention may be 200 to 300 MPa. This range is considered as an excellent range in the magnesium sheet according to an embodiment of the present invention.
  • a thickness of the magnesium alloy sheet according to an embodiment of the present invention may be 0.4 to 3 mm.
  • the magnesium sheet according to an embodiment of the present invention may be selected depending on properties required in the above thickness range. However, the present invention is not limited to this thickness range.
  • FIG. 1 is a flowchart schematically illustrating a manufacturing method for a magnesium alloy sheet according to an embodiment of the present invention.
  • the flowchart of the manufacturing method for a magnesium alloy sheet of FIG. 1 is merely to illustrate the present invention, and the present invention is not limited thereto. Therefore, the manufacturing method for a magnesium alloy sheet may be variously modified.
  • a manufacturing method for a magnesium alloy sheet includes: a step (S10) of preparing a cast material by casting a molten metal, the molten metal containing, relative to 100 wt% of the entire molten metal, 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 of Mg and other inevitable impurities; a step (S20) of subjecting the cast material to homogenization heat treatment; and a step (S30) of subjecting the cast material subjected to the homogenization heat treatment to warm-rolling.
  • the manufacturing method for a magnesium alloy sheet may further include other steps, as necessary.
  • the step (S10) of preparing a cast material by casting a molten metal may be performed, the molten metal containing, relative to 100 wt% of the entire molten metal, 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 of Mg and other inevitable impurities.
  • a die casting method a strip casting method, a billet casting method, a centrifugal casting method, a tilting casting method, a sand casting method, a direct chill casting method, or combination thereof may be used.
  • a strip casting method may be used.
  • the present invention is not limited thereto.
  • a rolling force may be 0.2 ton/mm 2 or more. Still more specifically, the rolling force may be 1 ton/mm 2 or more. Still more specifically, the rolling force may be 1.5 ton/mm 2 .
  • the cast material is coagulated and a rolling force is simultaneously applied thereto, and at this time, the formability of the magnesium alloy sheet may be improved by adjusting the rolling force to the above range.
  • step (S20) of subjecting the cast material to homogenization heat treatment may be carried out.
  • the heat treatment may be performed at a temperature of 350°C to 500°C for 1 to 28 hours. More specifically, the homogenization heat treatment may be performed for 18 to 28 hours.
  • the homogenization heat treatment is not properly performed, and beta phases such as Mg 17 Al 12 may not be solid-dissolved in the matrix.
  • the beta phases condensed in the cast material may melt, resulting in an occurrence of a fire or formation of holes in the magnesium sheet. Therefore, the homogenization heat treatment may be performed within the above-mentioned temperature range.
  • step (S30) of subjecting the cast material subjected to the homogenization heat treatment to warm-rolling may be carried out.
  • a temperature condition of the warm-rolling may be 150°C to 350°C.
  • a temperature range of lower than 150°C a large amount of edge cracks may be generated.
  • the magnesium alloy sheet In a temperature range of higher than of 500°C, the magnesium alloy sheet may not be appropriate for mass production. Therefore, the warm-rolling may be performed in the above-mentioned temperature range.
  • the step of subjecting the cast material subjected to the homogenization heat treatment to warm-rolling may be carried out a plurality of times, and the warm-rolling may be performed at a reduction ratio of 10 to 30% per time.
  • the reduction ratio of the warm-rolling refers to a "value(%)" relative to 100% of the thickness (length(%) of the cast material.
  • At least one time of a step of performing intermediate annealing in the middle of a plurality of times of warm-rolling may be further included.
  • the formability of the magnesium alloy sheet may be further improved.
  • the step of performing intermediate annealing may be carried out at 300 to 500°C for 1 to 10 hours. More specifically, the intermediate annealing step may be carried out at 450 to 500°C. Within the above-mentioned range, the formability of the magnesium alloy sheet may be further improved.
  • the method may further include a step of performing subsequent heat treatment.
  • the formability of the magnesium alloy sheet may be further improved.
  • the step of performing subsequent heat treatment may be carried out at 300 to 500°C for 1 to 15 hours. Specifically, the step of performing subsequent heat treatment may be carried out for 1 to 10 hours. Within the above-mentioned range, the formability of the magnesium alloy sheet may be further improved.
  • a manufacturing method for a magnesium alloy sheet may include: a step of preparing a cast material by casting a molten metal, the molten metal containing, relative to 100 wt% of the entire molten metal, 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 of Mg and other inevitable impurities; a step of subjecting the cast material to homogenization heat treatment; a step of preparing a rolled material by subjecting the cast material subjected to the homogenization heat treatment to warm-rolling; a step of subjecting the rolled material to subsequent heat treatment; and a step of producing a magnesium alloy sheet by subjecting the rolled material subjected to the subsequent heat treatment to skin pass.
  • the step of preparing a cast material by casting a molten metal may be performed, the molten metal containing, relative to 100 wt% of the entire molten metal, 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 of Mg and other inevitable impurities.
  • the molten metal may a commercially available AZ31 alloy, AL5083 alloy, or a combination thereof.
  • the present invention is not limited thereto.
  • the molten metal may be prepared in a temperature range of 650 to 750°C. Thereafter, a cast material may be produced by casting the molten metal. At this time, a thickness of the cast material may be 3 to 7 mm.
  • a die casting method a strip casting method, a billet casting method, a centrifugal casting method, a tilting casting method, a sand casting method, a direct chill casting method, or combination thereof may be used. More specifically, a strip casting method may be used. However, the present invention is not limited thereto.
  • a rolling force may be 0.2 ton/mm 2 or more. Still more specifically, the rolling force may be 1 ton/mm 2 or more. Still more specifically, the rolling force may be 1.5 ton/mm 2 .
  • the step of subjecting the cast material to homogenization heat treatment may be carried out.
  • the step of subjecting the cast material to homogenization heat treatment may include: a primary heat treatment step in a temperature range of 300°C to 400°C; and a secondary heat treatment step in a temperature range of 400°C to 500°C.
  • the temperature ranges of the primary heat treatment step and the secondary heat treatment step may be different from each other.
  • the primary heat treatment step in a temperature range of 300°C to 400°C may be carried out for 5 hours to 20 hours.
  • the secondary heat treatment step in a temperature range of 400°C to 500°C may be carried out for 5 hours to 20 hours.
  • a Mg-AI-Zn ternary system Pi-phase generated in the casting step may be removed.
  • the subsequent process may be adversely affected.
  • a stress in a slab may be released. Further, the formation of recrystallization of the cast structure may be more actively induced.
  • the step of preparing a rolled material by subjecting the cast material subjected to the homogenization heat treatment to warm-rolling may be carried out.
  • the cast material subjected to the heat treatment may be rolled to a thickness range of 0.4 to 3 mm through 1 to 15 times of rolling.
  • the rolling may be performed at 150 to 350°C.
  • the rolling temperature is lower than 150°C, a crack on the surface when rolling may be induced, and in a case where the rolling temperature is higher than 350°C, it may not be suitable for actual production facilities. Therefore, the rolling may be performed at 150°C to 350°C.
  • a step of subjecting the rolled material to intermediate annealing may be carried out.
  • heat treatment may be performed in a temperature range of 300°C to 550°C for 1 hour to 15 hours in an interval between the pass and the pass.
  • the intermediate annealing is performed one time after performing the rolling two times, and the rolled material may thus be rolled to the final target thickness.
  • the intermediate annealing is performed one time after performing the rolling three times, and the rolled material may thus be rolled to the final target thickness. More specifically, in a case where the rolled cast material is annealed in the above temperature range, the stress generated by the rolling may be released. Therefore, the rolling may be performed several times to obtain a desired thickness of the cast material.
  • the step of subjecting the rolled material to subsequent heat treatment may be carried out.
  • the step of subjecting the cast material to subsequent heat treatment may be carried out at 300 to 500°C for 1 to 15 hours. Specifically, the step of subjecting the cast material to subsequent heat treatment may be carried out for 1 to 10 hours. Within the above-mentioned range, the formability of the magnesium alloy sheet may be further improved.
  • the step of producing a magnesium alloy sheet by subjecting the rolled material subjected to the subsequent heat treatment to skin pass may be carried out.
  • the skin pass is also referred to as skin pass rolling or temper rolling, which means that a deformation pattern generated in a cold rolled sheet after heat treatment is removed, and cold rolling is performed with a light pressure to improve the strength.
  • the skin pass may be performed one time in a temperature range of 250°C to 350°C.
  • the magnesium alloy sheet produced by performing the skin pass may be rolled at a reduction ratio of 2 to 15% with respect to the thickness of the rolled material. More specifically, the reduction ratio may be related to the skin pass temperature.
  • the reduction ratio of the skin pass may be 5 to 15%.
  • a yield strength may be in a range of 200 to 260 MPa.
  • a limiting dome height may be in a range of 7.3 to 8.1.
  • the reduction ratio of the skin pass may be 5 to 15%. More preferably, the reduction ratio of the skin pass may be 7 to 12%.
  • a yield strength may be in a range of 200 to 250 MPa.
  • a limiting dome height may be in a range of 7.3 to 8.1.
  • a limit dome height is an index for evaluating formability of the sheet, in particular, pressability, and the formability may be measured by measuring a deformed height of a specimen obtained by applying a deformation to the specimen.
  • a high value of the limiting dome height means that the formability of the sheet is excellent.
  • the skin pass is performed under the conditions of the above temperature and pressure, the development of the texture of (0001) is suppressed, the formability may be secured. That is, in a case where the skin pass is performed under the above conditions, a change of the texture intensity may be minimized and the strength may thus be increased.
  • the molten metal was passed between two cooling rolls to prepare a magnesium cast material. At this time, a rolling force of the cooling roll is as shown in Table 1.
  • magnesium cast material was subjected to homogenization heat treatment at 400°C while varying time as shown in Table 1.
  • the magnesium cast material subjected to the homogenization heat treatment was subjected to warm-rolling at a temperature of 250°C at a reduction ratio of 15%.
  • the magnesium cast material subjected to the warm-rolling was subjected to intermediate annealing at a temperature as shown in Table 1, and then subjected to warm-rolling again at a temperature of 250°C at a reduction ratio of 15%, thereby producing a magnesium alloy sheet.
  • Example 1a Al content (wt%) Ca content (wt%) Casting roll Rolling force (ton/mm 2 ) Homogenization Annealing time (hr) Rolling temperature (C) Intermediate annealing temperature (C)
  • Example 1a 3 0.6 1.2 24 250 450
  • Example 1b 4 0.6 1.2 24 250 450
  • Example 1c 5 0.6 1 24 250 450
  • Example 1d 3 0.6 1.2 24 250 300
  • Example 1f 3 0.6 1.2 24 250 500 Example 1g 3 0.7 0.2 24 250 500
  • Example 1i 3 0.6 1 1 1 250 400 Comparative Example 1a 3 0.6 0.8 24 250 - Comparative Example 1b 3 0.7 1.2 24 400 250 Comparative Example 1c 3 0.7 1 48 250 400 Comparative Example 1d 3 0.7 0.8 24 100 400
  • FIGS. 2 to 4 of the present invention The observed results are illustrated in FIGS. 2 to 4 of the present invention.
  • FIG. 2 is a photograph obtained by observing a magnesium alloy sheet produced in Example 1a with a scanning electron microscope (SEM).
  • FIG. 3 is a photograph obtained by observing a magnesium alloy sheet produced in Comparative Example 1a with a scanning electron microscope (SEM).
  • a horizontal direction is a rolling direction (RD) of the magnesium alloy sheet and a vertical direction is a thickness direction (ND) of the magnesium alloy sheet.
  • RD rolling direction
  • ND thickness direction
  • Example 1a center segregation of the magnesium alloy sheet was hardly generated in Example 1a. Specifically, it can be appreciated that a ratio of a length of the center segregation to the total length of about 2000 ⁇ m in the rolling direction in Example 1a was less than 5%.
  • FIG. 4 is a photograph obtained by observing the magnesium alloy sheet produced in Example 1a with secondary electron microscopy.
  • the white dots in FIG. 4 are Al-Ca secondary phase particles. More specifically, as a result of analyzing compositions of the white dots in FIG. 4 , it was analyzed that the white dots contain 24.61 wt% of Al, 8.75 wt% of Ca, 0.36 wt% of Mn, 0.66 wt% of Zn, and the balance of Mg and other inevitable impurities.
  • the magnesium alloy sheet produced in Example 1a includes the Al-Ca secondary phase particles. Specifically, it can be appreciated that 50 Al-Ca secondary phase particles were distributed per area of 1600 ⁇ m 2 of the magnesium alloy sheet in FIG. 4 .
  • Example 1a As illustrated in FIG. 4 , it can be appreciated that the center segregation of the Al-Ca secondary phase particles was not generated in Example 1a, and the Al-Ca secondary phase particles were dispersed. From this fact, as shown in Table 2, it can be appreciated that a limiting dome height of the magnesium alloy sheet produced in Example 1a of the present invention is 9.4 mm, whereas a limiting dome height of the magnesium alloy sheet produced in Comparative Example 1a is 2.5 mm, which shows that the formability of the magnesium alloy sheet produced in Comparative Example 1a is inferior to that of the magnesium alloy sheet produced in Example 1a.
  • a limit dome height is an index for evaluating formability of the sheet, in particular, pressability, and the formability may be measured by measuring a deformed height of a specimen obtained by applying a deformation to the specimen.
  • the limiting dome height was measured by inserting each of the magnesium alloy sheets of examples and comparative examples between an upper die and a lower die, and fixing an outer periphery of each specimen with a force of 5 kN.
  • a known press oil was used as a lubricant.
  • a spherical punch having a diameter of 20 mm was used to deform the specimen at a rate of 5 to 10 mm/min, the punch was inserted until each specimen was fractured, and then a deformed height of each specimen at the time of fracturing was measured. That is, the deformed height of the specimen was measured.
  • FIG. 5 shows a result of measuring a limiting dome height of the magnesium alloy sheet produced in Example 1a.
  • Example 1a As illustrated in FIG. 5 , it can be appreciated that the magnesium alloy sheet produced in Example 1a has an excellent formability.
  • the pole figure is represented by stereographic projection of an orientation of an arbitrarily fixed crystal coordinate system onto a coordinate system of the specimen.
  • poles of the crystal grains with various orientations with respect to a ⁇ 0001 ⁇ surface are represented on a standard coordinate system, and a density contour of the poles is drawn according to a pole density distribution, thereby representing the pole figure.
  • the poles are fixed in a specific lattice direction by Bragg's angle, and a plurality of poles may be represented for a single crystal.
  • FIG. 6 shows a maximum texture intensity of a (0001) surface of Example 1a.
  • FIG. 7 shows a maximum texture intensity of a (0001) surface of Comparative Example 1a.
  • the maximum texture intensity of each of the (0001) surfaces of FIGS. 6 and 7 is the result obtained by analyzing the crystal orientation of the magnesium alloy sheet with the XRD analyzer as described above.
  • the maximum density distribution value (texture intensity) of the (0001) surface in examples was 2.73, which is low, whereas the maximum density distribution value in comparative examples was 12.1, which is high as compared to that of each example.
  • the magnesium alloy sheets of examples have a more excellent formability.
  • FIGS. 8 and 9 This may be appreciated through FIGS. 8 and 9 of the present invention.
  • FIG. 8 shows a result of electron backscatter diffraction (EBSD) analysis of the magnesium alloy sheet produced in Example 1a.
  • EBSD electron backscatter diffraction
  • FIG. 9 is a graph illustrating fractions of crystal orientations of Example 1a.
  • the crystal orientation of crystal grain may also be measured by EBSD. More specifically, the crystal orientation of crystal grain may be measured by EBSD by injecting electrons into a specimen through e-electron beam and using inelastic scattering diffraction at the back of the specimen.
  • crystal grains having a misorientation angle of 20° or less between grains may be bottom crystal grains. Therefore, it was confirmed that the volume fraction of the crystal grains in the ⁇ 0001>//C-axis direction relative to 100% of the volume fraction of the entire crystal grains was about 18.5%.
  • Example 1i 17 1 164 9 Comparative Example 1a 10 0.7 188 2.5 Comparative Example 1b 11 0.6 155 5 Comparative Example 1c 40 1.5 145 5.1 Comparative Example 1d 8 1 166 4.9
  • Comparative Examples of 1a to 1d which did not satisfy the conditions of homogenization annealing time, rolling temperature, and intermediate annealing temperature, the formability was inferior to that of each example.
  • a yield strength of each of Comparative Examples of 1a to 1d was inferior to that of each example.
  • an average size of the crystal grains was about 40 ⁇ m, that is, the formability was relatively excellent as compared to that of the other comparative examples, but a level of the formability was less than that of each example.
  • a molten metal containing, relative to 100 wt% of the entire molten metal, 3.0 wt% of Al, 0.1 wt% of Zn, 1.0 wt% of Ca, 0.3 wt% of Mn, and the balance of Mg and inevitable impurities was prepared.
  • the molten metal was casted to prepare a magnesium cast material.
  • the magnesium cast material was subjected to a primary homogenization heat treatment at 350°C for 10 hours.
  • the magnesium cast material subjected to the primary homogenization heat treatment was subjected to a secondary homogenization heat treatment at 450°C for 10 hours.
  • a rolled material was prepared by casting the cast material subjected to homogenization heat treatment.
  • a magnesium alloy sheet was produced in the same manner as that of Example 2, except for the conditions of skin pass temperature and reduction ratio.
  • the formability may be measured by comparing numerical values of an elongation rate and a limiting dome height.
  • the formability may be secured by minimizing the change of the texture, and the change of the texture depending on the reduction ratio of the skin pass may be confirmed through FIG. 10 .
  • FIG. 10 is a result of EBSD analysis of a magnesium alloy sheet depending on a reduction ratio of skin pass.
  • the area fraction of the twinned crystal structure, relative to 100% of the entire area of the magnesium alloy was 15%. It was confirmed that in a case where the reduction ratio of the skin pass is 6 to 15%, the area fraction of the twinned crystal structure, relative to 100% of the entire area of the magnesium alloy, was 30%.
  • the strength of the magnesium alloy sheet may be maintained and the formability of the magnesium alloy sheet may also be improved.
  • FIG. 11 shows a maximum texture intensity of each of (0001) surfaces of Example 2 and Comparative Example 2, depending on a skin pass condition.

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