US20220010413A1 - Magnesium alloy sheet and manufacturing method therefor - Google Patents

Magnesium alloy sheet and manufacturing method therefor Download PDF

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Publication number
US20220010413A1
US20220010413A1 US17/280,722 US201917280722A US2022010413A1 US 20220010413 A1 US20220010413 A1 US 20220010413A1 US 201917280722 A US201917280722 A US 201917280722A US 2022010413 A1 US2022010413 A1 US 2022010413A1
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magnesium alloy
alloy sheet
relational expression
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sheet
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Jun Ho Park
Jae Joong Kim
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Posco Holdings Inc
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Posco Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C23/00—Alloys based on magnesium
    • C22C23/04—Alloys based on magnesium with zinc or cadmium as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
    • B21B37/58—Roll-force control; Roll-gap control
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C22C23/06—Alloys based on magnesium with a rare earth metal 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 thereof.
  • the crystal structure of magnesium is HCP structure, and the c/a ratio of unit cell is higher than that of materials with other HCP structures, so only the basal slip-based ⁇ 0001 ⁇ 11-20> can be activated at room temperature.
  • the C-axis of the HCP is aligned with the thickness direction of the rolled plate, making it more difficult to accommodate the C-axis deformation.
  • the present invention has been made in an effort to provide a magnesium alloy sheet having advantages of excellent formability at room temperature and activation of the slip of the non-bottom surface by controlling the relationship between gadolinium (Gd) and zinc (Zn).
  • An exemplary embodiment of the present invention provides a magnesium alloy sheet.
  • Another embodiment of the present invention provides a method for manufacturing a magnesium alloy sheet.
  • gadolinium (Gd) and zinc (Zn) By controlling the relationship between gadolinium (Gd) and zinc (Zn), it is possible to disperse the texture of the magnesium alloy sheet, and activation of the slip base of the non-bottom surface may be easy. Accordingly, it is intended to possess formability at a level of the aluminum alloy for automobiles.
  • a magnesium alloy sheet according to an exemplary embodiment of the present invention may comprises: 0.1 to 1.5 wt % of Zn, 0.08 to 0.7 wt % of Gd, a remainder of Mg, and other inevitable impurities with respect to an entire 100 wt % of the magnesium alloy sheet, and the magnesium alloy sheet may satisfy Relational Expression 1 below.
  • the [Zn] and [Gd] may indicate wt % of each component.
  • Relational Expression 1 may be 3.0 or more and 15.0 or less.
  • Relational Expression 1 may be 3.0 or more and 13.0 or less.
  • the magnesium alloy sheet may further comprise 0.3 wt % or less of Mn (excluding 0 wt %) with respect to the total of 100 wt % of the magnesium alloy sheet.
  • the magnesium alloy sheet may comprise a secondary phase, and the number of secondary phases per an area of 40000 ⁇ m 2 of the magnesium alloy plate may be 1 to 20.
  • the average particle diameter of the secondary phase may be 0.1 to 3 ⁇ m.
  • An average crystal grain size of the magnesium alloy sheet may be 5 to 30 ⁇ m.
  • the limited dome height (LDH) of the magnesium alloy sheet may be 10.5 mm or more.
  • An edge crack of the magnesium alloy sheet may be 5 mm or less.
  • the magnesium alloy plate may have maximum texture intensity of 4.5 or less with respect to the (0001) plane
  • a method for manufacturing a magnesium alloy sheet according to another exemplary embodiment of the present invention may comprise: preparing a casting material by casting an alloy melt solution comprising 0.1 to 1.5 wt % of Zn, 0.08 to 0.7 wt % of Gd, a remainder of Mg, and other inevitable impurities for the entire 100 wt %, homogenizing and heat-treating the casting material, preparing a rolled material by rolling the homogenized and heat-treated casting material, finally annealing the rolled material, and the alloy melt solution may satisfy Relational Expression 1 below.
  • the [Zn] and [Gd] may indicate wt % of each component.
  • Relational Expression 1 may be 3.0 or more and 15.0 or less.
  • Relational Expression 1 may be 3.0 or more and 13.0 or less.
  • the alloy melt solution may comprise 0.3 wt % or less of Mn (excluding 0 wt %) with respect to the total of 100 wt % of the alloy melt solution.
  • the homogenizing and heat-treating of a casting material may perform at a temperature of 300 to 500° C.
  • the homogenizing and heat-treating of a casting material may perform for 5 hour or more.
  • the preparing of a rolled material may comprise performing rolling at a temperature of 150 to 350° C.
  • the preparing of a rolled material comprises performing a rolling with a reduction ratio that is greater than 0 and equal to or less than 30% for each rolling.
  • gadolinium (Gd) and zinc (Zn) By controlling the relationship between gadolinium (Gd) and zinc (Zn), it is possible to possess formability at a level of the aluminum alloy for automobiles.
  • FIG. 1 shows binary phase diagram of Mg—Gd.
  • FIG. 2 shows the maximum dissolved amount of Gd at 400° C. according to the added element.
  • FIG. 3 shows an observation of a microstrure step-by-step of Example 1 and Comparative Example 4 with Optical Microscopy.
  • FIG. 4 shows the results of analysis of the (0001) planes of Example 2, Example 3 and Comparative Example 4 by XRD method of pole figure.
  • a magnesium alloy sheet according to an exemplary embodiment of the present invention may comprise: 0.1 to 1.5 wt % of Zn, 0.08 to 0.7 wt % of Gd, a remainder of Mg, and other inevitable impurities with respect to an entire 100 wt % of the magnesium alloy sheet.
  • Zn may be comprised at 0.1 to 1.5 wt %. Specifically, it may be comprised at 1 to 1.5 wt %.
  • the effect of dispersing the texture may increase.
  • a Zn element when a Zn element is less than 0.1 wt %, the effect of improving formability and rollability may be insignificant. On the other hand, when a Zn element is more than 1.5 wt %, mechanical properties and formability may be deteriorated due to an increase in the secondary phase fraction and coarsening.
  • 0.08 to 0.7 wt % of Gd may be comprised. Specifically, 0.1 to 0.6 wt % of Gd may be comprised. More specifically, 0.1 to 0.05 wt % of Gd may be comprised.
  • a Gd element may be dissolved and segregated in the grain boundary or the twin boundary. Segregation signifies that solute elements are concentrated in a certain area. In an exemplary embodiment of the present invention, segregation may signify that solute elements are concentrated in a grain boundary or a twin boundary.
  • the Gd element may be segregated in the above-described interfaces.
  • the segregated Gd element may give a solute dragging effect and may accelerate the dispersion of the texture during rolling and heat-treating processes.
  • the effect of dispersing the texture may be more excellent.
  • the Gd element When the Gd element is more than 0.7 wt %, the size and fraction of Mg 5 Gd and MgZn secondary phase may increase. In this case, it may give a negative influence on the formability. Further, as the Gd element is more than 0.7 wt %, the content of Zn must be also more than 2.1 wt % for the value of the Relational expression 1 ([Zn]/[Gd]) to be described below to be 3.0 or more. Therefore, mechanical properties and formability may be deteriorated due to an increase in the secondary phase fraction and coarsening.
  • the magnesium alloy sheet may satisfy Relational Expression 1 below.
  • the [Zn] and [Gd] may indicate wt % of each component.
  • a ratio of wt % of zinc (Zn) to wt % of gadolinium (Gd) may be 3.0 or more. Specifically, the ratio may be 3.0 or more and 15.0 or less. Specifically, the ration may be 13.0 or less. Specifically, by controlling the weight ratio of Zn to Gd described above, Gd and Zn are simultaneously dissolved in the boundary, so that a solute dragging effect may be excellent.
  • the weight ratio of Zinc (Zn) to Gadolinium (Gd) is less than 3
  • the mount of Gd and Zn elements segregated together at a grain boundary and a twin boundary may be reduced. Therefore, the degree of a solute dragging effect of segregated elements may be lowered. That is, the more the amount of segregation dissolved, the more the slip base of the non-bottom surface is activated, so that the formability may be improved.
  • the solute segregation is typically distributed along the basal slip of the surface, and thus the basal slip of the surface can be controlled.
  • the gap in the degree of activation between the two slip systems is reduced, and the probability of activating the non-bottom slip may increase.
  • the weight ratio of Zn to Gd is more than 15.0, it may comprise too little Gd or too much Zn. In this case, the effect of improving formability may be insignificant. Alternatively, workability and formability may be deteriorated due to an increase in the secondary phase fraction and coarsening.
  • the magnesium alloy sheet may further comprise 0.3 wt % or less of Mn (excluding 0 wt %) with respect to the total of 100 wt % of the magnesium alloy sheet.
  • the manganese forms a Fe—Mn-based compound to thus function to reduce the content of the component of Fe in the sheet. That is, it is easy to control Fe impurities.
  • the reason why the upper limit of the Mn component is limited to 0.3 wt % is that when manganese is added in an amount more than 0.3 wt %, the Gd solubility becomes low and the formability is deteriorated.
  • formability when manganese is comprised in the range above, formability may be excellent. More specifically, an alloy with a small addition amount of an alloying element may have excellent bendability, thermal conductivity, and corrosion resistance.
  • the magnesium alloy sheet may comprise a secondary phase, and the number of secondary phases per an area of 40000 ⁇ m 2 of the magnesium alloy plate may be 1 to 20.
  • the secondary phase may be Mg 5 Gd, MgZn, or a combination thereof.
  • the average particle diameter of the secondary phase may be 0.1 to 3 ⁇ m.
  • the average particle diameter and the number of secondary phases may be the result of controlling the composition range of the above-described alloy component and Relational Expression 1.
  • the activation of the slip base of the non-bottom surface may be improved. Therefore, a magnesium alloy sheet excellent in formability may be provided.
  • An average crystal grain size of the magnesium alloy sheet may be 5 to 30 ⁇ m
  • the formability when the average crystal grain size of the magnesium alloy sheet is within the range above, the formability may be more excellent. More specifically, when it is smaller than the range above, the formability at room temperature may be deteriorated. When it is larger than the range above, the formability at high temperature may be deteriorated.
  • the limited dome height (LDH) of the magnesium alloy sheet may be 10.5 mm or more. Specifically, the limited dome height (LDH) of the magnesium alloy sheet may be 1 mm or more.
  • the limited dome height means a value derived through the Erichsen test at room temperature. The formability of the material may be compared through the limited dome height (LDH).
  • An edge crack of the magnesium alloy sheet may be 5 mm or less. Specifically, an edge crack of the magnesium alloy sheet may be 1 mm or less.
  • the edge crack means a groove formed at the edge of the surface of the magnesium alloy sheet.
  • the edge crack may be caused when the workability is low. That is, the higher the formability of the alloy is, the better the workability is, so the edge cracks may be reduced.
  • the edge crack of the magnesium alloy sheet according to an exemplary embodiment of the present invention may be within the range above.
  • the edge crack when the edge crack is within the range above, the formability may be excellent. More specifically, the edge crack may be caused more by the Al 2 Ca secondary phase, but the alloy according to an exemplary embodiment of the present invention does not contain a Ca component and does not have the secondary phase described above, so that the edge crack may be reduced and thus the magnesium alloy sheet excellent in the formability may be provided.
  • the magnesium alloy plate may have maximum texture intensity of 4.5 or less with respect to the (0001) plane. Specifically, the magnesium alloy plate may have a maximum texture intensity of 1.0 to 4.5 or less.
  • the texture intensity with respect to the (0001) plane is within the range above, the fraction of the crystal grain on the bottom surface may be small, and the activation of the slip base of the non-bottom surface may be easy. Therefore, a magnesium alloy sheet excellent in formability may be provided.
  • a method for manufacturing a magnesium alloy sheet according to another exemplary embodiment of the present invention may comprise: preparing a casting material by casting an alloy melt solution comprising 0.1 to 1.5 wt % of Zn, 0.08 to 0.7 wt % of Gd, a remainder of Mg, and other inevitable impurities for the entire 100 wt %, homogenizing and heat-treating the casting material, preparing a rolled material by rolling the homogenized and heat-treated casting material, finally annealing the rolled material.
  • the reason for limiting the component and composition of the alloy melt solution corresponds to the above-described reason for limiting the component and the composition of the magnesium alloy sheet, so it will not be described.
  • the alloy melt solution may satisfy the Relational Expression 1 below.
  • the [Zn] and [Gd] may indicate wt % of each component.
  • the temperature of the alloy melt solution may be 650 to 750° C.
  • the magnesium alloy may be cast in the range above.
  • the temperature when the temperature is lower than 650° C., the fusion of the magnesium alloy may not be performed properly. On the other hand, when the temperature is higher than 750° C., it may be difficult to manage the melt solution due to ignition.
  • Preparing the casting material may be performed as casting the above-described alloy melt solution.
  • it may be cast through strip casting, gravity casting, or a combination thereof.
  • the method is not limited thereto.
  • a step of homogenizing and heat-treating the casting material may be performed.
  • a step of homogenizing and heat-treating the casting material may be performed at a temperature of 300 to 500° C. Specifically, homogenizing and heat-treating the casting material may be performed for 1 hour or more.
  • the temperature is 300° C. or higher, dissolution of a gadolinium (Gd) element may be possible. Further, the higher the temperature is, the higher the dissolved amount of gadolinium. However, when the temperature is higher than 500° C., the surface of the casting material may be oxidized. Therefore, it may not be suitable for the mass production process.
  • Gd gadolinium
  • the step of preparing the rolled material may be performed at a temperature of 150 to 350° C.
  • rolling may be possible without an edge crack when a temperature of 150° C. or higher is secured. Rolling at the higher than 350° C. may not be in accord with mass production realistically. Rolling with a reduction ratio that is greater than 0 and equal to or less than 30% for each rolling may be performed.
  • a reduction ratio means that the difference between the thickness of the material before passing through the rolling roll during rolling and the thickness of the material after passing through the rolling roll is divided by the thickness of the material before passing through the rolling roll and multiplied by 100.
  • rolling may be performed several times at the reduction ratio to roll to the final target thickness.
  • Preparing the rolling material may further comprise intermediately annealing the rolled material.
  • Intermediately annealing the rolled material may be performed at a temperature of 300 to 500° C.
  • it may be performed for 10 minutes to 15 hours.
  • intermediately annealing the rolled material may be performed after two consecutive rolling.
  • intermediately annealing the rolled material may be performed after three consecutive rolling.
  • it may be rolled without intermediate annealing.
  • the stress generated during rolling may be sufficiently relieved.
  • the final annealing of the rolled material may be performed in a temperature range of 300 to 500° C.
  • it may be performed for 10 minutes to 15 hours.
  • Recrystallization may be easily formed by final annealing under the conditions above.
  • the Erichsen value of the magnesium alloy sheet manufactured through the above-described process may be 10.5 mm or more. Specifically, it may be 11.0 mm or more.
  • the above value may mean room temperature formability similar to a level of conventional aluminum metal.
  • Example and Comparative Example An alloy melt solution of Example and Comparative Example was prepared according to the wt % of the alloy components disclosed in Table 1 below.
  • melt solution was cast by a strip casting method to prepare the cast material.
  • the cast material was then homogenized and heat-treated at 400° C. for 7 hours.
  • the homogenized and heat-treated cast material was rolled at 300° C. at a reduction rate of about 20% per rolling. Intermediate annealing was also performed in the middle of the rolling. Specifically, it was performed at 400° C. for an hour.
  • the thickness of the manufactured magnesium alloy sheet was 0.4 to 1.8 mm.
  • a magnesium alloy sheet with a horizontal length and a vertical length of respectively 50 to 60 mm is used, and a lubricant is used on an exterior side of the sheet so as to reduce friction between the sheet and a spherical punch.
  • the die and the spherical punch are at room temperature.
  • the magnesium alloy sheet is inserted between an upper die and a lower die, an exterior circumference portion of the sheet is fixed with a force of 10 kN, and the sheet is deformed at a speed of 5 mm/min by using a spherical punch with a diameter of 20 mm. The punch is inserted until the sheet is broken, and when it is broken, a deformed height of the sheet is measured.
  • the above-described deformed height of the sheet is referred to as an Erichsen value or a limited dome height (LDH). From this, it is possible to compare the formability of the sheet. Specifically, the higher the deformed height of the magnesium alloy sheet is, the higher the Erichsen value and the higher the formability may be.
  • LDH limited dome height
  • an exemplary embodiment of the present invention may not comprise aluminum. When it comprises aluminum, It may not be possible to dissolve Gd.
  • FIG. 1 shows binary phase diagram of Mg—Gd.
  • FIG. 1 shows the phase diagram of Mg—Zn0.5 wt %-xGd, and it may be seen that the dissolved amount of Gd at 400° C.
  • FIG. 2 it is possible to derive FIG. 2 by drawing a phase diagram according to the content of each element as shown in FIG. 1 .
  • FIG. 2 shows the maximum dissolved amount of Gd at 400° C. according to the added element.
  • FIG. 2 shows the measurement of the amount of Gd that may be dissolved when the phase diagram of the three elements Al, Zn, and Mg is prepared as in the Mg—Gd binary phase diagram of FIG. 1 .
  • an exemplary embodiment of the present invention may not comprise aluminum.
  • aluminum may exist as a level of an impurity.
  • it may comprise 0.005 wt % or less of aluminum.
  • Comparative Example 1 comprising Gd alone, it may be confirmed that the result of low formability compared to the Examples of the present specification is an Erichsen value at room temperature of 4.6 mm.
  • Examples of the present specification may be formability at room temperature similar to a level of conventional aluminum metal.
  • A15083 among commercially available aluminum alloys, has an Erichsen value of about 12 mm at room temperature.
  • FIG. 3 shows the microstructures of Example 1 and Comparative Example 4 by observing with an optical microscopy.
  • Example 1 As shown in the photo after the heat treatment of FIG. 3 , it may be confirmed visually that the number of secondary phases in Example 1 is significantly smaller than that of Comparative Example 4. More specifically, in the case of Example 1, it may be seen that the number of secondary phases per area of 40000 ⁇ m 2 is less than about 20. On the other hand, Comparative Example 4 may be seen that more than the Example at the level of 50 to 100 per the same area.
  • the secondary phase is Mg 5 Gd and MgZn.
  • Comparative Example 4 as a result of adding more than the range of gadolinium (Gd) according to an exemplary embodiment of the present invention, it may be seen that the particle diameter of the secondary phase is coarse and the fraction of the secondary phase is larger than that of the Example.
  • Gd gadolinium
  • the Erichsen value at room temperature of Comparative Example 4 is 9.3 mm, whereas the Erichsen value at room temperature of Example 1 is 11.0 mm, indicating that the formability at room temperature is more excellent.
  • the fraction and size of the secondary phase may be controlled through the composition range of gadolinium (Gd) and the relationship between gadolinium and zinc (Zn/Gd) as in the Examples of the present specification, thereby reducing factors that hinder deformation behavior.
  • FIG. 4 shows the results of analyzing the (0001) plane of Example 2 and 3 and Comparative Example 4 by the XRD method of pole figure.
  • the pole figure is shown by a stereoscopic projection of the direction of an arbitrarily fixed crystal coordinate system onto the specimen coordinate system. That is, poles with respect to the (0001) plane of crystal grains of various orientations may be displayed in the reference coordinate system, and the pole figure may be represented by drawing a density contour line according to the pole density distribution. In this instance, the pole is fixed in a specific lattice direction by the Bragg angle, and multiple poles may be displayed for a monocrystalline.
  • a numerical expression of the density distribution value of the contour line represented by the method of pole figure may be referred to as the maximum texture intensity for the (0001) plane.
  • Example 3 has a slightly higher maximum aggregation strength value than Comparative Example 4.
  • shape of the pole figure in Example 3 is similar to that of Comparative Example 4.
  • Methods of improving the workability of the magnesium alloy sheet comprise a method of dispersing the texture and a method of the slip base of the non-bottom surface. Specifically, considering that the shape of the pole figure is similar in Example 3 and Comparative Example 4, it is possible to derive a relatively random orientation of the crystal grains.
  • Comparative Example 4 is a case in which more than the range of gadolinium (Gd) is added according to an exemplary embodiment of the present invention.
  • the Zn/Gd value of Comparative Example 4 was 1.28, and a value less than 3 was derived. That is, it may be seen that Comparative Example 4 does not satisfy the composition of gadolinium and the Zn/Gd value of the Relational expression 1 according to an exemplary embodiment of the present invention.
  • the value according to the Relational expression 1 is less than 3, the amount of gadolinium and zinc segregated at the grain boundary or the twin boundary may be reduced, and thus the slip base of the non-bottom surface may be deteriorated.
  • the formability of the alloy sheet having better activation of the slip base of the non-base surface may be more excellent.
  • the formability of the alloy sheet having a smaller size of the secondary phase and a lower fraction of the secondary phase may be excellent.
  • the slip base of the non-bottom surface may be activated.
  • the content of the gadolinium (Gd) component decreases, so deformation behavior may be easy.
  • the present invention is not limited to the above-mentioned exemplary 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, it should be understood that the exemplary embodiments described above are illustrative and non-limiting in all respects.

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KR1020180116033A KR102178806B1 (ko) 2018-09-28 2018-09-28 마그네슘 합금 판재 및 이의 제조방법
KR10-2018-0116033 2018-09-28
PCT/KR2019/012409 WO2020067704A1 (fr) 2018-09-28 2019-09-24 Tôle d'alliage de magnésium et procédé de fabrication associé

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CN113444945B (zh) * 2021-07-02 2022-04-26 云南大学 一种具有环形发散织构的高塑性、高成形性镁合金板材及其制备方法
CN113462940B (zh) * 2021-07-02 2022-04-26 云南大学 一种具有室温高成形性的镁合金板材及其制备方法
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