[go: up one dir, main page]
More Web Proxy on the site http://driver.im/

US20190093200A1 - Magnesium alloy sheet and method for manufacturing same - Google Patents

Magnesium alloy sheet and method for manufacturing same Download PDF

Info

Publication number
US20190093200A1
US20190093200A1 US16/065,562 US201616065562A US2019093200A1 US 20190093200 A1 US20190093200 A1 US 20190093200A1 US 201616065562 A US201616065562 A US 201616065562A US 2019093200 A1 US2019093200 A1 US 2019093200A1
Authority
US
United States
Prior art keywords
magnesium alloy
alloy sheet
heat treatment
rolling
manufacturing
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.)
Abandoned
Application number
US16/065,562
Other languages
English (en)
Inventor
Jun Ho Park
Oh Duck Kwon
Hyun Bom LEE
Jae Joong Kim
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Posco Holdings Inc
Original Assignee
Posco Co Ltd
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Priority claimed from KR1020150185017A external-priority patent/KR20170075407A/ko
Priority claimed from KR1020150186295A external-priority patent/KR101751521B1/ko
Application filed by Posco Co Ltd filed Critical Posco Co Ltd
Assigned to POSCO reassignment POSCO ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: KIM, JAE JOONG, KWON, OH DUCK, LEE, HYUN BOM, PARK, JUN HO
Publication of US20190093200A1 publication Critical patent/US20190093200A1/en
Assigned to POSCO HOLDINGS INC. reassignment POSCO HOLDINGS INC. CHANGE OF NAME (SEE DOCUMENT FOR DETAILS). Assignors: POSCO
Assigned to POSCO CO., LTD reassignment POSCO CO., LTD ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: POSCO HOLDINGS INC.
Abandoned legal-status Critical Current

Links

Images

Classifications

    • 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

  • the invention relates to a magnesium alloy sheet, and method for manufacturing thereof.
  • magnesium is the lightest metal with a density of 1.744 g/cm 3 such as aluminum and steel and has various advantages such as vibration absorbing ability and electromagnetic shielding capability as compared with other structural materials, therefore Related industry researches are being actively carried out to utilize them.
  • Such an alloy comprising magnesium are currently being applied not only in the field of electronic devices but also in the field of vehicle, but they have fundamental problems in corrosion resistance, flame resistance, and formability, therefore there are limitations in expanding the application range.
  • magnesium is a HCP structure (Hexagonal Closed Packed Structure), and there is not enough slip system at room temperature, making it difficult to progress. That is, a large amount of heat is required in the magnesium processing process, this leads to an increase in the cost of the processing process.
  • HCP structure Hexagonal Closed Packed Structure
  • the AZ system magnesium alloys comprise aluminum (Al) and zinc (Zn), which are inexpensive and yet commercially available magnesium alloys, securing adequate strength and physical properties of ductile.
  • the physical properties mentioned above mean that it has an appropriate level among the magnesium alloys, and the strength is lower than that of aluminum (Al), which is competitive material.
  • the present invention is intended to provide a method of manufacturing magnesium alloy sheet with improved strength and formability.
  • a magnesium alloy sheet according to an embodiment of the present invention contains 2.7 to 5 wt % of Al, 0.75 to 1 wt % of Zn, 0.1 to 1 wt % of Ca and 1 wt % or less (Excluding 0 wt %) of Mn, and consists of the balance of Mg and inevitable impurities.
  • the magnesium alloy sheet alloy sheet may comprise Al—Ca secondary phase particles comprising 20 to 25% wt % of Al, 5 to 10% wt % of Ca, 0.1 to 0.5% wt % of Mn, 0.5 to 1% of Zn and the balance of Mg.
  • the average particle size of the Al—Ca secondary phase particles may be 0.01 to 4 ⁇ m.
  • the Al—Ca secondary phase particles may comprise 5 to 15 per 100 ⁇ m 2 of the magnesium alloy sheet.
  • the magnesium alloy sheet may comprise crystal grain and the average particle size of the crystal grain is 5 to 30 ⁇ m.
  • the thickness of the magnesium alloy sheet may be 0.4 to 3 mm.
  • a method for manufacturing a magnesium alloy sheet according to an embodiment of the present invention comprises the steps of casting a molten metal containing 2.7 to 5 wt % of Al, 0.75 to 1 wt % of Zn, 0.1 to 1 wt % of Ca and 1 wt % or less (Excluding 0 wt %) of Mn and consisting of the balance of Mg and inevitable impurities to produce a casted material; subjecting the casted material to homogenization heat treatment; and warm-rolling the casted material subjected to homogenization treatment.
  • the reduction pressure may be 0.2 ton/mm 2 or more. More specifically, it may be 1 ton/mm 2 or more. More specifically, it may be 1 to 1.5 ton/mm 2 or more.
  • Subjecting the casted material to homogenization heat treatment may be carried out for 1 to 28 hours at a temperature of 350 to 500° C. More specifically, it may be subjected to homogenization heat treatment for 18 to 28 hours.
  • Warm-rolling may be at a temperature of 150 to 350° C. More specifically, warm-rolling may be at a temperature of 200 to 300° C.
  • Warm-rolling may be performed a plurality of times, and warm-rolling may be at a reduction ratio of 10% to 30% per time.
  • It may further comprise the step of intermediate annealing in the middle of a plurality of times of warm-rolling.
  • the intermediate annealing may be carried out at a temperature of 300 to 500° C. More specifically, it may be carried out at a temperature of 450 to 500° C. More specifically, it may be carried out for 1 to 10 hours.
  • the step of subjecting to subsequent heat treatment may comprise further after the step of warm-rolling,
  • the step of subjecting to subsequent heat treatment may be carried out for 1 to 10 hours at a temperature of 300 to 500° C.
  • a method for manufacturing a magnesium alloy sheet may comprise the steps of preparing a master alloy comprising 2.7 wt % or more and 5 wt % or less of Al, 0.75 wt % or more and 1 wt % or less of Zn, 0.1 wt % or more and 1 wt % or less of Ca, more than 0 wt % and 1 wt % or less of Mn and the balance of inevitable impurities and magnesium, for a total of 100 wt %; casting the master alloy to produce a casted material; subjecting the casted material to homogenization heat treatment; warm-rolling the casted material subjected to homogenization heat treatment to produce a rolled material; subjecting the rolled material to subsequent heat treatment; and carrying out a skin pass to the rolled material subjected to subsequent heat treatment to produce a magnesium alloy sheet.
  • the skin pass may be carried out once, and it may be carried out at a temperature in the range of 250° C. to 350° C.
  • the produced magnesium alloy sheet may be rolled at a reduction ratio of 2 to 15% with respect to the thickness of the rolled material. More specifically, the produced magnesium alloy sheet may be rolled at a reduction ratio of 2 to 6% with respect to the thickness of the rolled material.
  • the step of subjecting the casted material to homogenization heat treatment may comprise a first heat treatment step at a temperature in the range of 300° C. to 400° C.; and a second heat treatment step at a temperature in the range of 400° C. to 500° C.
  • a first heat treatment step at a temperature in the range of 300° C. to 400° C. may be carried out for 5 to 20 hours.
  • a second heat treatment step at a temperature in the range of 400° C. to 500° C. may be carried out for 5 to 20 hours.
  • the casted material may be rolled to a thickness of 0.4 to 3 mm.
  • the casted material may be rolled 1 to 15 times.
  • the step of rolling the casted material subjected to homogenization heat treatment to produce a rolled material may be carried out at 150° C. to 350° C.
  • the rolled material may be annealed at a temperature in the range of 300° C. to 550° C. for 1 to 15 hours.
  • the limiting dome height (LDH) of the magnesium alloy sheet may be 7 mm or more. More specifically, the limiting dome height (LDH) of the magnesium alloy sheet may be 8 mm or more.
  • a maximum aggregate strength may be 1 to 4 on the basis of the magnesium alloy sheet (0001) surface.
  • the yield strength of the magnesium alloy sheet may be 170 to 300 MPa.
  • it may provide a magnesium alloy sheet that the center segregation which is likely to be generated in the conventional magnesium alloy sheet is removed and the formability is improved.
  • it may provide a magnesium alloy sheet in which the texture of the magnesium alloy sheet is homogeneously dispersed, and the formability of which is improved.
  • it may provide a magnesium alloy sheet that the secondary phase particle of Al—Ca system are formed in a magnesium alloy sheet and strength is improved.
  • a method for manufacturing a magnesium alloy sheet according to an embodiment of the present invention may provide a magnesium alloy sheet which is excellent in strength and formability by controlling the manufacturing process of a commercially available magnesium alloy. Because of this, it may be applied to appliances of vehicle or IT mobile devices in the future.
  • FIG. 1 is a schematic flowchart of a method of manufacturing a magnesium alloy sheet according to an embodiment of the present invention.
  • FIG. 2 is an image of scanning electron microscope (SEM) of the magnesium alloy sheet produced in Example 1.
  • FIG. 3 is an image of scanning electron microscope of the magnesium alloy sheet produced in Comparative Example 1.
  • FIG. 4 is an image of a Secondary Electron Microscopy of the magnesium alloy sheet produced in Example 1.
  • FIG. 5 is an image of a result of measuring the limiting dome height of the magnesium alloy sheet produced in Example 1.
  • FIG. 6 is a result of analysis of the crystal orientation by the XRD analyzer of the magnesium alloy sheet produced in Example 1.
  • FIG. 7 is a result of analysis of the crystal orientation by the XRD analyzer of the magnesium alloy sheet produced in Comparative Example 1.
  • FIG. 8 is an image of Electron Backscatter Diffraction (EBSD) of the magnesium alloy sheet produced in Example 1.
  • FIG. 9 is a result of EBSD analysis of the surface according to the reduction ratio in the skin pass process.
  • FIG. 10 shows the aggregate strength of the (0001) surface of Examples and Comparative Examples of the present invention.
  • the first term, second and third term, etc. are used to describe various parts, components, regions, layers and/or sections, but are not limited thereto. These terms are only used to distinguish any part, component, region, layer or section from other part, component, region, layer or section. Therefore, the first part, component, region, layer or section may be referred to as the second part, component, region, layer or section within the scope unless excluded from the scope of the present invention.
  • % means weight % (wt %) unless otherwise referred.
  • the magnesium alloy sheet according to an embodiment of the present invention contains 2.7 to 5 wt % of Al, 0.75 to 1 wt % of Zn, 0.1 to 1 wt % of Ca, 1 wt % or less of Mn (excluding 0 wt %) and consist of the balance of Mg and inevitable impurities.
  • Al (AI) improves the mechanical properties of the magnesium alloy sheet and castability of the molten metal. If Al is added too much, the castability may deteriorate rapidly, and if too little Al is added, the problem that mechanical properties deteriorate may occur. Therefore, the content range of Al may be adjusted within the range mentioned above.
  • Zinc (Zn) improves the mechanical properties of the magnesium alloy sheet. If too much Zn is added, a large number of surface defects and center segregation may be generated, leading to a problem of rapidly deteriorated castability, and if too little Zn is added, the problem that mechanical properties of magnesium alloy sheet deteriorate may occur. Therefore, the content range of Zn may be adjusted within the range mentioned above.
  • Ca Calcium (Ca) gives flame resistance to the magnesium alloy sheet. If too much Ca is added, the fluidity of the molten metal is reduced, the castability becomes worse, and the center segregation made of the Al—Ca system intermetallic material is generated, which may cause a problem of deteriorating the formability of the magnesium alloy sheet, and if too little is added, the problem that the flame resistance is not sufficiently given may occur. Therefore, the content range of Ca may be adjusted within the range mentioned above. More specifically, Ca may be comprised 0.3 to 0.8% (wt %).
  • Manganese (Mn) improves the mechanical properties of the magnesium alloy sheet material. If too much Mn is added, the problems that the heat emission is reduced and at the same time, uniform distribution control is difficult, may occur. Therefore, the content range of Mn may be adjusted within the above-mentioned range.
  • the magnesium alloy sheet alloy sheet according to embodiment of the present invention may comprise Al—Ca secondary phase particles comprising 20 to 25% wt % of Al, 5 to 10% wt % of Ca, 0.1 to 0.5% wt % of Mn, 0.5 to 1% of Zn and the balance of Mg.
  • Al—Ca secondary phase particles comprising 20 to 25% wt % of Al, 5 to 10% wt % of Ca, 0.1 to 0.5% wt % of Mn, 0.5 to 1% of Zn and the balance of Mg.
  • the magnesium alloy sheet according to an embodiment of the present invention may improve formability by comprising Al—Ca secondary phase particles.
  • the average particle diameter of the Al—Ca secondary phase particles may be 0.01 to 4 ⁇ m. The formability may be further improved in the above-mentioned range.
  • the Al—Ca secondary phase particles may be comprised 5 to 15 particles per 100 ⁇ m 2 square of the magnesium alloy sheet material.
  • the formability of the magnesium alloy sheet may be further improved.
  • the composition ranges of Al. Zn, Mn, and Ca the temperature and time conditions during the homogenization heat treatment, the temperature and the rolling rate during warm rolling are necessary to be precisely controlled.
  • the magnesium alloy sheet comprise crystal grain and the average particle size of the crystal grain is 5 to 30 ⁇ m.
  • the formability may be further improved within the range mentioned above.
  • the composition scopes of Al. Zn, Mn, and Ca the temperature and time conditions during the homogenization heat treatment, the temperature and the rolling rate during warm rolling are necessary to be precisely controlled.
  • the limiting dome height of the magnesium alloy sheet according to an embodiment of the present invention may be 7 mm or more. More specifically, it may be 8 mm or more, more specifically 8 to 10 mm.
  • the limiting dome height is as an index for evaluating the formability (especially, compressibility) of the material, it means that the formability of the material is improved as such the limiting dome height increases.
  • the limited range mentioned above is, significantly higher limiting dome height than magnesium alloy sheet generally known, which caused by an increase in the distribution of crystal grain orientation in magnesium alloy sheet.
  • the thickness of the magnesium alloy sheet according to an embodiment of the present invention may be 0.4 to 3 mm.
  • FIG. 1 schematically shows a flow chart of a method manufacturing a magnesium alloy sheet according to an embodiment of the present invention.
  • the flow chart of a method manufacturing a magnesium alloy sheet of FIG. 1 is only to illustrate the present invention and is not limited thereto. Therefore, the method of manufacturing a magnesium alloy sheet may be variously modified.
  • a method of manufacturing a magnesium alloy sheet according to an embodiment of the present invention comprises the steps of casting a molten metal containing 2.7 to 5 wt % of Al, 0.75 to 1 wt % of Zn, 0.1 to 1 wt % of Ca and 1 wt % or less (Excluding 0 wt %) of Mn and consisting of the balance of Mg and inevitable impurities to produce a casted material (S 10 ); subjecting the casted material to homogenization heat treatment (S 20 ); and warm-rolling the casted material subjected to homogenization treatment (S 30 ).
  • the manufacturing method of the magnesium alloy sheet may further comprise other steps.
  • a molten metal containing 2.7 to 5 wt % of Al, 0.75 to 1 wt % of Zn, 0.1 to 1 wt % of Ca and 1 wt % or less (Excluding 0 wt %) of Mn and consisting of the balance of Mg and inevitable impurities is casted to produce a casted material.
  • a method of casting the casted material are die casting, strip casting, centrifugal casting, tilting casting, sand casting, direct chill casting or a combination thereof. More specifically, strip casting may be used. However, the present invention is not limited thereto.
  • the reduction pressure may be 0.2 ton/mm 2 or more. More specifically, it may be 1 ton/mm2 or more. More specifically, it may be 1 to 1.5 ton/mm 2 or more.
  • the casted material may be produced by casting. At this time, when the casted material is coagulated and reduction pressure is simultaneously applied, the formability of the magnesium alloy sheet may be improved by adjusting the reduction pressure to the range mentioned above.
  • the casted material is subjected to homogenization heat treatment.
  • the heat treatment condition may be at a temperature of 350 to 500° C. for 1 to 28 hours. More specifically, it may be subjected to homogenization heat treatment for 18 to 28 hours. If the temperature is too low, the homogenization treatment cannot be properly performed, and there may occur a problem that beta phases such as Mg 17 Al 12 are not be employed at the base. If the temperature is too high, beta phases condensed the casted material may melt, resulting in a fire or resulting in holes on the magnesium sheet. Therefore, it may be subjected to homogenization heat treatment within the temperature range described above.
  • the homogenized casted material is warm-rolled.
  • the temperature condition of the warm-rolling may be at a temperature of 150 to 350° C. If the temperature is too low, there may occur a problem generating large amount of edge crack. If the temperature is too high, there may occur a problem being inappropriate for mass production. Therefore, warm-rolling may be within the above-mentioned temperature range.
  • the step of warm-rolling may be performed a plurality of times, and warm-rolling may be at a reduction ratio of 10% to 30% per time. By carrying out warm-rolling a plurality of times, finally, it may be rolled to a thin thickness of 0.4 mm.
  • the formability of the magnesium alloy sheet may be further improved by comprising the step of intermediate annealing. More specifically, the step of intermediate annealing may be carried out at a temperature of 300 to 500° C. for 1 to 10 hours. More specifically, it may be carried out at a temperature of 450 to 500° C. The formability of the magnesium alloy sheet may be improved within the range mentioned above.
  • subjecting to the subsequent heat treatment may be further comprised.
  • the formability of the magnesium alloy sheet may be improved by comprising the step of subjecting to the subsequent heat treatment.
  • the step of subjecting to the subsequent heat treatment may be carried out at a temperature of 300 to 500° C. for 1 to 10 hours.
  • the formability of the magnesium alloy sheet may be further improved within the above-mentioned range.
  • a method for manufacturing a magnesium alloy sheet according to an embodiment of the present invention may comprise the steps of preparing a master alloy comprising 2.7 wt % or more and 5 wt % or less of Al, 0.75 wt % or more and 1 wt % or less of Zn, 0.1 wt % or more and 0.7 wt % or less of Ca, more than 0 wt % and 1 wt % or less of Mn and the balance of inevitable impurities and magnesium, for a total of 100 wt %; casting the master alloy to produce a casted material; subjecting the casted material to homogenization heat treatment; warm-rolling the casted material subjected to homogenization heat treatment to produce a rolled material; subjecting the rolled material to subsequent heat treatment; and carrying out a skin pass to the rolled material subjected to subsequent heat treatment to produce a magnesium alloy sheet.
  • the master alloy may be commercially available AZ31 alloy, AL5083 alloy or a combination thereof. However, it is not limited thereto.
  • the step of casting the master alloy to produce a casted material may be carried out.
  • the master alloy may be dissolved to prepare the molten metal at the temperature range of 650 to 750° C. Thereafter, the molten metal may be cast to produce a casted material. At this time, the thickness of the casted material may be 3 to 7 mm.
  • a method of casting the casted material are die casting, strip casting, centrifugal casting, tilting casting, sand casting, direct chill casting or a combination thereof. More specifically, strip casting may be used. However, it is not limited thereof.
  • the reduction pressure may be 0.2 ton/mm 2 or more. More specifically, it may be 1 ton/mm 2 or more. More specifically, it may be 1 to 1.5 ton/mm 2 or more.
  • the step of subjecting the casted material to homogenization heat treatment may be carried out.
  • the step of subjecting the casted material to homogenization heat treatment may comprise the step of a first heat treatment at a temperature scope of 300° C. to 400° C.; and the step of a second heat treatment at a temperature scope of 400° C. to 500° C. More specifically, the step of first heat treatment at a temperature range of 300° C. to 400° C. may be carried out for 5 to 20 hours. In addition, the step of second heat treatment at a temperature range of 400° C. to 500° C. may be carried out for 5 to 20 hours.
  • the Mg—Al—Zn ternary system Pi-phase generated in the casting step may be removed. If the ternary system Pi-phase exists, the subsequent process may be adversely affected. In addition, the stress in the slab may be released by carrying out the second heat treatment step within the above-mentioned temperature range. Furthermore, it may actively induce the formation of recrystallization of the cast structure in the slab.
  • the step of warm-rolling the casted material subjected to homogenization heat treatment to produce the rolled material may be carried out.
  • the heat-treated slab may be rolled to a thickness range of 0.4 to 3 mm through 1 to 15 times of rolling.
  • the rolling may be carried out at a temperature of 150° C. to 350° C.
  • the rolling temperature is less than 150° C., it may induce a crack on the surface when rolling, and if it exceeds 350° C., it may not be suitable for actual production facilities. Therefore, it may be rolled at 150° C. to 350° C.
  • the step of intermediate annealing the rolled material may be carried out.
  • it When it is rolled several times in the step of rolling, it may be subjected to heat treatment at the temperature range of 300° C. to 550° C. for 1 to 15 hours in the interval between the pass and the pass.
  • it may be subjected to intermediate annealing once after rolling twice, and then rolled to a final target thickness.
  • it may be rolled to the final target thickness by annealing once after rolling three times. More specifically, in the case where the rolled casted material is annealed in the above temperature range, the stress generated by rolling may be released. Therefore, it may be rolled several times up to the desired thickness of the casted material.
  • the step of carrying out a skin pass to the rolled material subjected to subsequent heat treatment to produce a magnesium alloy sheet may be performed.
  • the skin pass is also known as skin pass rolling or temper rolling, which means that it removes a deformation pattern generated in a cold rolled steel sheet after heat treatment, and cold rolling with light pressure to improve the hardness.
  • a skin pass may be carried out once at a temperature range of 250° C. to 350° C. More specifically, the magnesium alloy sheet manufactured by carrying out 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, may be rolled at a reduction ratio of 2 to 6%. More specifically, in the case of rolling under the conditions of the temperature and the pressure, the development of the texture, which is a weak base surface texture (0001) is reduced, so that formability may be obtained.
  • the magnesium alloy sheet manufactured by the step of carrying out a skin pass to the annealed rolled material to produce a magnesium alloy sheet may be rolled at a reduction ratio of 2 to 15% with respect to the thickness of the rolled slab. More specifically, it may be rolled at a reduction ratio of 2 to 6%.
  • the strength may be improved by minimizing the change in the strength of the texture. More specifically, when the reduction ratio is 2 to 6%, the change in the strength of the texture is the smallest and the yield strength may be 170 to 300 MPa. In addition, the value of the limiting dome height (LDH) may be 8 to 9 mm.
  • the yield strength may be 250 to 280 MPa, but value of the limiting dome height may be 7 to 8 mm since the texture is somewhat developed.
  • the area fraction of the twinned crystal structure may be 5% or less with respect to 100% of the total area of the magnesium alloy sheet.
  • the area fraction of the twinned crystal structure may be 5 to 20% with respect to 100% of the total area of the magnesium alloy sheet.
  • a black color means twinned crystal structure, and as described above, the strength of the magnesium alloy sheet is maintained and the formability may be improved due to twinned crystal and dislocation.
  • the texture of the (0001) surface may be developed again and the formability may be lowered. This may be the same phenomenon that occurs when the temperature range during rolling is low. Therefore, the skin pass may be carried out under the condition of temperature range and the reduction ratio according to an embodiment of the present invention.
  • LDH Limit Dome Height
  • the limit dome height (LDH) is measured the distance at which punch moved until the disc-shaped specimen was fractured, that is, the height at which the specimen was deformed, by fixing a peripheral portion of a specimen having a diameter of 50 mm with a force of 10 KN and then applying a deformation at a rate of 5 to 10 mm/min using a spherical punch having a diameter of 20 mm at a room temperature.
  • a molten metal comprising 3.0 wt % of Al, 0.8 wt % of Zn, 0.6 wt % of Ca, 0.5 wt % of Mn and consisting of the balance of Mg and inevitable impurities was passed through between two cooling rolls having a reduction pressure of 1.2 ton/mm 2 to produce a magnesium casted material.
  • the magnesium alloy sheet having a final thickness of 0.7 mm was produced by carrying out subjecting the magnesium casted material to homogenization heat treatment at a temperature of 400° C. for 24 hours, warm-rolling at 250° C. at a reduction ratio of 15%, intermediate annealing at 450° C. for 1 hour, and warm-rolling again at 250° C. at a reduction ratio of 15%.
  • a magnesium alloy sheet was produced in the same manner as in Example 1, except that 3.0 wt % of Al and 0.8 wt % of Zn were comprised.
  • Test Example 1 Observation of Microstructure that Composes a Magnesium Alloy Sheet
  • Example 1 In the case of Example 1 ( FIG. 2 ), the central segregation of the magnesium alloy sheet was hardly generated, whereas in the case of Comparative Example 1 ( FIG. 3 ), it may be confirmed that a large amount of central segregation occurred. Such center segregation becomes a factor of being deteriorated the formability of the magnesium alloy sheet.
  • the white dot portion in FIG. 4 is Al—Ca secondary phase particles.
  • analysis was made with 65.62 wt % of Mg, 24.61 wt % of Al, 8.75 wt % of Ca, 0.36 wt % of Mn and 0.66 wt % of Zn.
  • Test Example 2 Measurement of Limit Dome Height of a Magnesium Alloy Sheet
  • the limit dome height was determined by inserting each magnesium alloy sheet of the Examples and the Comparative examples between the upper die and the lower die and fixing the outer periphery of each specimen with a force of 5 kN and the press oil was used as the lubricant. Then, a spherical punch having a diameter of 30 mm was used to deform at a rate of 5 to 10 mm/min, the punch was inserted until each specimen was fractured and then it was performed when occurring such fracture in the manner of measuring of the deformation height of each specimen.
  • FIG. 5 is an image of a result of measuring the limit dome height of the magnesium alloy sheet produced in Example 1.
  • Test Example 3 Analysis of Crystal Grain Orientation
  • Example 1 The crystal orientation of each of the crystal grains of the magnesium alloy sheet produced in Example 1 and Comparative Example 1 confirmed by an XRD analyzer and was shown in FIG. 6 and FIG. 7 respectively.
  • Example 1 In the case of Example 1 ( FIG. 6 ), contour lines are widely spread, and it may be confirmed that the crystal orientation of the crystal grains in the sheet are presented widely and variously. Therefore, it may be confirmed that the formability of Example 1 is excellent. On the other hand, in the case of Comparative Example 1 ( FIG. 7 ), it may be confirmed that the (0001) peak is concentrated.
  • a master alloy comprising 3% of Al, 1% of Zn, 1% of Ca, 0.3% of Mn and the balance of magnesium and inevitable impurities was prepared.
  • the master alloy was cast to produce a casted material.
  • the casted material was subjected to a first homogenization heat treatment at a temperature of 350° C. for 10 hours.
  • the casted material subjected to a first homogenization heat treatment was subjected to a secondary homogenization heat treatment at a temperature of 450° C. for 10 hours.
  • the casted material subjected to homogenization heat treatment was rolled to produce a rolled material. Thereafter, the rolled material was subjected to subsequent heat treatment at a temperature of 400° C. for 10 hours.
  • the yield strength was improved without greatly changing the formability. More specifically, the formability may be compared with the numerical values of the elongation and the limit dome height.
  • FIG. 10 shows the aggregate strength of (0001) surface of the Examples and Comparative Examples of the present invention.
  • Example 3 As compared with Example 1, a magnesium alloy sheet material was produced under different conditions as disclosed in Table 2 below. As a result, the mechanical properties of the magnesium alloy sheet produced in Example 3 are disclosed in Table 3 below.
  • the present invention is not limited to the above-mentioned examples or embodiments and may be manufactured in various forms, those who have ordinary knowledge of the technical field to which the present invention belongs may understand that it may be carried out in different and concrete forms without changing the technical idea or fundamental feature of the present invention. Therefore, the above-mentioned examples or embodiments are illustrative in all aspects and not limitative.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Metal Rolling (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
US16/065,562 2015-12-23 2016-12-23 Magnesium alloy sheet and method for manufacturing same Abandoned US20190093200A1 (en)

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
KR10-2015-0185017 2015-12-23
KR1020150185017A KR20170075407A (ko) 2015-12-23 2015-12-23 마그네슘 합금판, 및 그 제조방법
KR1020150186295A KR101751521B1 (ko) 2015-12-24 2015-12-24 마그네슘 합금 판재 제조방법
KR10-2015-0186295 2015-12-24
PCT/KR2016/015228 WO2017111550A1 (ko) 2015-12-23 2016-12-23 마그네슘 합금 판재, 및 그 제조방법

Publications (1)

Publication Number Publication Date
US20190093200A1 true US20190093200A1 (en) 2019-03-28

Family

ID=59091071

Family Applications (1)

Application Number Title Priority Date Filing Date
US16/065,562 Abandoned US20190093200A1 (en) 2015-12-23 2016-12-23 Magnesium alloy sheet and method for manufacturing same

Country Status (5)

Country Link
US (1) US20190093200A1 (ja)
EP (1) EP3395458B1 (ja)
JP (1) JP6758383B2 (ja)
CN (1) CN108472699B (ja)
WO (1) WO2017111550A1 (ja)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US11773472B2 (en) * 2017-12-26 2023-10-03 Posco Co., Ltd Magnesium alloy sheet and method for producing same

Families Citing this family (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20190000676A (ko) * 2017-06-23 2019-01-03 주식회사 포스코 마그네슘 합금 판재 및 이의 제조방법
KR102043287B1 (ko) * 2017-12-26 2019-11-11 주식회사 포스코 마그네슘 합금 판재 및 이의 제조방법
CN108796327B (zh) * 2018-06-28 2020-08-28 郑州大学 一种高塑性、低各向异性变形镁合金板材及其制备方法
KR102239185B1 (ko) * 2018-12-18 2021-04-12 주식회사 포스코 성형성이 우수한 마그네슘 합금 판재의 제조방법 및 이로부터 제조된 마그네슘 합금 판재
WO2021040988A1 (en) * 2019-08-26 2021-03-04 Ohio State Innovation Foundation Magnesium alloy based objects and methods of making and use thereof
CN113005347B (zh) * 2021-02-25 2021-10-08 吉林大学 一种高塑性Mg-Al-Ca镁合金及其制备方法
CN113416873B (zh) * 2021-06-28 2023-01-20 晋中学院 高电磁屏蔽效能稀土镁合金板材及其制备方法
CN113770175B (zh) * 2021-09-30 2024-08-06 重庆大学 一种低温大道次压下量轧制无边裂镁合金板材的方法

Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5158675B2 (ja) * 2007-06-27 2013-03-06 三菱アルミニウム株式会社 耐食性及び表面処理性に優れるマグネシウム合金板材とその製造方法
KR101078308B1 (ko) * 2008-05-19 2011-10-31 포항공과대학교 산학협력단 고강도 마그네슘 합금 판재 및 그 제조방법
JP2010156007A (ja) * 2008-12-26 2010-07-15 Mitsubishi Alum Co Ltd 耐食性及び表面処理性に優れるマグネシウム合金板材とその製造方法
JP2010229467A (ja) * 2009-03-26 2010-10-14 Hitachi Metals Ltd マグネシウム合金薄板の製造方法
JP5424391B2 (ja) * 2009-09-30 2014-02-26 国立大学法人長岡技術科学大学 マグネシウム合金圧延材並びにその製造方法
JP5590660B2 (ja) * 2010-03-01 2014-09-17 独立行政法人産業技術総合研究所 冷間成形性と面内異方性を改善したマグネシウム合金板材及びその作製方法
JP5660525B2 (ja) * 2010-03-05 2015-01-28 独立行政法人産業技術総合研究所 アルミニウム合金並みの常温成形性を発揮する汎用マグネシウム合金板材及びその製造方法
KR101481909B1 (ko) * 2013-08-08 2015-01-13 주식회사 포스코 마그네슘 합금의 제조 방법
KR101626820B1 (ko) * 2013-12-05 2016-06-02 주식회사 포스코 마그네슘 합금 판재 및 이의 제조 방법

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US11773472B2 (en) * 2017-12-26 2023-10-03 Posco Co., Ltd Magnesium alloy sheet and method for producing same

Also Published As

Publication number Publication date
WO2017111550A8 (ko) 2017-09-28
EP3395458A1 (en) 2018-10-31
CN108472699A (zh) 2018-08-31
JP6758383B2 (ja) 2020-09-23
JP2019504207A (ja) 2019-02-14
CN108472699B (zh) 2021-12-28
EP3395458A4 (en) 2018-10-31
WO2017111550A1 (ko) 2017-06-29
EP3395458B1 (en) 2021-08-18

Similar Documents

Publication Publication Date Title
US20190093200A1 (en) Magnesium alloy sheet and method for manufacturing same
US11268171B2 (en) Aluminum alloy foil, and method for producing aluminum alloy foil
US11566311B2 (en) Aluminum alloy foil, and method for producing aluminum alloy foil
KR102043774B1 (ko) 고성형 마그네슘 합금 판재 및 이의 제조방법
US20180105900A1 (en) High-strength aluminum alloy sheet
JP7274585B2 (ja) マグネシウム合金板材およびその製造方法
KR20190078281A (ko) 마그네슘 합금 판재 및 이의 제조방법
US11739400B2 (en) Magnesium alloy and method for manufacturing the same
KR20170075407A (ko) 마그네슘 합금판, 및 그 제조방법
US20210147964A1 (en) Magnesium alloy sheet and manufacturing method therefor
US20170349978A1 (en) Aluminum alloy sheet
KR101610360B1 (ko) 마그네슘 합금판, 및 이의 제조방법
KR101716669B1 (ko) 마그네슘 합금판의 제조방법
CN110114486A (zh) 镁合金板材及其制造方法
JP2019044270A (ja) アルミニウム合金箔およびアルミニウム合金箔の製造方法
US11149330B2 (en) Magnesium alloy plate and method for manufacturing same
KR102252289B1 (ko) 마그네슘 합금 판재 및 그 제조방법
JP2019007038A (ja) プレス成形性および耐デント性に優れた自動車パネル用アルミニウム合金板
KR102190501B1 (ko) 박물주조용 고강도 및 고성형성 알루미늄 합금판재 및 이의 제조방법
KR20190015066A (ko) 마그네슘 합금 판재 및 이의 제조방법

Legal Events

Date Code Title Description
AS Assignment

Owner name: POSCO, KOREA, REPUBLIC OF

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNORS:PARK, JUN HO;KWON, OH DUCK;LEE, HYUN BOM;AND OTHERS;REEL/FRAME:046186/0460

Effective date: 20180524

STPP Information on status: patent application and granting procedure in general

Free format text: DOCKETED NEW CASE - READY FOR EXAMINATION

STPP Information on status: patent application and granting procedure in general

Free format text: NON FINAL ACTION MAILED

STPP Information on status: patent application and granting procedure in general

Free format text: RESPONSE TO NON-FINAL OFFICE ACTION ENTERED AND FORWARDED TO EXAMINER

STPP Information on status: patent application and granting procedure in general

Free format text: NON FINAL ACTION MAILED

STPP Information on status: patent application and granting procedure in general

Free format text: RESPONSE TO NON-FINAL OFFICE ACTION ENTERED AND FORWARDED TO EXAMINER

STPP Information on status: patent application and granting procedure in general

Free format text: FINAL REJECTION MAILED

STPP Information on status: patent application and granting procedure in general

Free format text: DOCKETED NEW CASE - READY FOR EXAMINATION

STPP Information on status: patent application and granting procedure in general

Free format text: NON FINAL ACTION MAILED

STPP Information on status: patent application and granting procedure in general

Free format text: RESPONSE TO NON-FINAL OFFICE ACTION ENTERED AND FORWARDED TO EXAMINER

STPP Information on status: patent application and granting procedure in general

Free format text: FINAL REJECTION MAILED

STPP Information on status: patent application and granting procedure in general

Free format text: ADVISORY ACTION MAILED

STCB Information on status: application discontinuation

Free format text: ABANDONED -- FAILURE TO RESPOND TO AN OFFICE ACTION

AS Assignment

Owner name: POSCO HOLDINGS INC., KOREA, REPUBLIC OF

Free format text: CHANGE OF NAME;ASSIGNOR:POSCO;REEL/FRAME:061561/0705

Effective date: 20220302

AS Assignment

Owner name: POSCO CO., LTD, KOREA, REPUBLIC OF

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNOR:POSCO HOLDINGS INC.;REEL/FRAME:061774/0129

Effective date: 20221019