WO2019027188A1 - Tôle d'alliage de magnésium et son procédé de fabrication - Google Patents

Tôle d'alliage de magnésium et son procédé de fabrication Download PDF

Info

Publication number
WO2019027188A1
WO2019027188A1 PCT/KR2018/008565 KR2018008565W WO2019027188A1 WO 2019027188 A1 WO2019027188 A1 WO 2019027188A1 KR 2018008565 W KR2018008565 W KR 2018008565W WO 2019027188 A1 WO2019027188 A1 WO 2019027188A1
Authority
WO
WIPO (PCT)
Prior art keywords
magnesium alloy
less
alloy sheet
heat treatment
sheet material
Prior art date
Application number
PCT/KR2018/008565
Other languages
English (en)
Korean (ko)
Inventor
김상현
권오덕
채영욱
김재중
Original Assignee
주식회사 포스코
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 KR1020170180319A external-priority patent/KR102045063B1/ko
Application filed by 주식회사 포스코 filed Critical 주식회사 포스코
Publication of WO2019027188A1 publication Critical patent/WO2019027188A1/fr

Links

Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/46—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting
    • 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
    • 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
    • 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
    • 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

  • the present invention relates to a magnesium alloy sheet and a method of manufacturing the same.
  • the density of magnesium is 1.74 g / cin 3 , which is the lightest among structural metals including aluminum and steel. In addition, it is a metal that is popular in mobile and IT fields due to its excellent vibration absorbing ability and electromagnetic shielding ability. In addition,
  • magnesium is expensive compared to competitive materials such as aluminum and stainless steel, its application is limited to only some parts that are required to be lightweight.
  • magnesium has hexagonal close packing (HCP)
  • HCP hexagonal close packing
  • An object of the present invention is to provide a magnet alloy sheet material excellent in room temperature moldability, anisotropy and corrosion resistance and a method for manufacturing the same.
  • the content and relationship of Zn, Mn, and Ce components can be controlled to control impurities and secondary phases of the magnesium alloy sheet material. From this, it is possible to provide a magnet alloy sheet material excellent in corrosion resistance, moldability, and anisotropy.
  • the magnesium alloy sheet according to one embodiment of the present invention has a zinc (Zn) content of more than 0 to 2.0 wt%, a manganese (Mn) content of more than 0 to 1.0 wt%, a cerium (Ce) %, Residual magnesium (Mg), and other unavoidable impurities.
  • the magnesium alloy sheet material may satisfy the following relational expression (1).
  • [Zn], [Mn], and [Ce] refer to weight percent of each component.
  • the other unavoidable impurities may include Al: 0.3 wt% or less and Fe: 100 ppm or less.
  • the thickness ratio of the center segregation to the thickness of the magnesium alloy sheet material may be 10% or less.
  • the average particle size of the Mg-Ce phase and lower phase is 0. To 20 / m, and 1 to 30 per 100 2 of the magnesium alloy sheet material.
  • the average grain size of the Mn-based secondary may contain one or more sugar ⁇ 1 to 15, the area 100 / of the magnesium alloy plate and m 2.
  • the base aggregate maximum aggregate strength of the magnet alloy sheet material may be 1 or more and 4 or less.
  • the magnesium alloy sheet may have an Erickson value at room temperature of 7 to 11 mm.
  • the magnesium alloy sheet material may have a corrosion rate of 2.0 / / y or less.
  • the magnesium alloy sheet material may have a critical bending radius value at room temperature of 4 R / t or less.
  • the magnesium alloy sheet may have a limit bending radius value at 200 o C of 1.5 R / t or less.
  • the magnesium alloy sheet material may have a difference between the rolling direction (RD) and the plate material width direction (TD) by 0.5 R / t or less.
  • the cerium may be either a cerium element alone or a cerium-
  • the mis-metal may further include other rare earth elements.
  • (Mn) is more than 0 and not more than 1.0 wt%
  • cerium (Ce) is not more than 0 and not more than 2.0 wt%
  • manganese Comprises a step of preparing a cast material by casting a molten alloy containing from 0 to 0.5% by weight, the balance being magnesium (Mg) and other unavoidable impurities, subjecting the cast material to homogenization heat treatment, Hot rolling to prepare a rolled plate material, and finally heat-treating the rolled plate material.
  • the molten alloy of the alloy could satisfy the following relational expression (1).
  • [Zn], [Mn], and [Ce] refer to weight of each component.
  • the other gross-smelling impurities may include Al: 0.3 wt% or less and Fe: 100 ppm or less.
  • the step of subjecting the cast material to a homogenizing heat treatment may be performed at a temperature of 300 ° C
  • the step of homogenizing the cast material is performed for 1 to 30 hours .
  • the step of subjecting the cast material to homogenization heat treatment may include a first homogenization heat treatment step and a second homogenization heat treatment step.
  • the primary homogenizing heat treatment is also 300 degrees (0 C) to 400 may be live-action in (° C). Specifically, it may be carried out for 0.5 to 10 hours.
  • the second homogenization heat treatment may be carried out 400 degrees (0 C) to about 500 in FIG. (° C). Specifically, it may be carried out for 0.5 to 20 hours.
  • the step of hot-rolling the homogenized heat-treated cast material to prepare the rolled plate may be performed at a temperature of 150 ° C to 400 ° C.
  • it can be carried out at a rolling reduction of not less than 0 and not more than 40% per rolling.
  • the step of rolling the homogenized heat-treated cast material to prepare a rolled plate may further include intermediate-annealing the rolled plate.
  • the intermediate annealing is performed at least once during the warm rolling of the rolled sheet material twice or more, and the cumulative rolling reduction of the rolled sheet material may be 40% or more.
  • the intermediate annealing execution rate may be 20% or less.
  • the intermediate annealing may be performed 300 degrees (0 C) to about 500 in FIG. (° C).
  • the intermediate annealing may be conducted for 5 hours or less (excluding 0 hours).
  • the step of final annealing the rolled sheet can be carried out 250 degrees (° C) to 500 in Figure (0 C).
  • it may be conducted for 5 hours or less (excluding 0 hours).
  • the present invention it is possible to provide a magnesium alloy plate excellent in room temperature moldability and corrosion resistance by adding a small amount of Mn and Ce to a Zn-based magnesium alloy and controlling the production step.
  • the impurities and the secondary phase (intermetallic compound) of the magnesium alloy sheet can be controlled by controlling the content and relationship of Zn, Mn, and Ce. From this, it is possible to provide a magnesium alloy sheet material excellent in corrosion resistance. Further, it is possible to provide a magnesium alloy sheet material excellent in moldability by dispersing the bottom surface texture. In addition, by controlling the center segregation of the secondary phase, it is possible to provide a magnesium alloy plate excellent in anisotropy.
  • FIG. 1 is a photograph of a microstructure of the microstructure after (a) and (b) after homogenization heat treatment in Example 2 and Comparative Example 4 under an optical microscope.
  • SEM scanning electron microscopy
  • BSE backscattered eletron
  • Fig. 4 is a comparison of the ⁇ 0001 ⁇ XRD pattern of the embodiment and the comparative example.
  • FIG. 5 is a photograph of the ⁇ 0001 ⁇ XRD pattern and EBSD of Example 2 and Comparative Example 5.
  • FIG. 5 is a photograph of the ⁇ 0001 ⁇ XRD pattern and EBSD of Example 2 and Comparative Example 5.
  • FIG. 6 is a graph showing the results of V-bending test at room temperature (a) and 200 ° C (b) of Example 2, showing microstructure in the direction of RD (Rolling Diode) Was observed with an optical microscope.
  • the magnesium alloy sheet according to one embodiment of the present invention may contain zinc (Zn) in an amount of 0 to 2.0 wt% or less, manganese (Mn) in an amount of 0 to 1.0 wt% or less, cerium (Ce) in an amount of 0 By weight, up to 0.5% by weight, residual magnesium (Mg) and other unavoidable impurities.
  • the magnesium alloy sheet material may satisfy the following relational expression (1)
  • [Zn], [Mn], and [Ce] refer to weight percent of each component.
  • the content of the Zn component may be larger than the sum of the Mn and Ce components, as in the relational expression (1).
  • the magnesium alloy sheet material may have a good rolling property and moldability.
  • manganese serves to control impurities such as iron (Fe) and silicon (Si). Therefore, when manganese is contained in the above range, the content of impurities contained in the magnesium alloy sheet material can be effectively reduced owing to the above-described characteristics.
  • the Fe content in other unavoidable impurities contained in 100 weight 3 ⁇ 4 of the magnesium alloy sheet as a whole may be 100 ppm or less. Also, the A1 content was
  • the kind of the impurity is not limited thereto, and may include other unavoidable impurities.
  • the corrosion resistance, rolling property and moldability of the magnesium alloy sheet material can be improved.
  • the magneto-alloy plate according to one embodiment may further include aluminum (A1).
  • Aluminum may be included in an amount of 0.3% by weight or less based on the entire magnesium alloy sheet material.
  • the composition range of the aluminum component is not particularly limited,
  • a magnesium alloy sheet according to an embodiment of the present invention May be added to the impurity level as compared to the additive element.
  • the zinc (Zn) may be contained in an amount of more than 0 to 2.0% by weight, preferably 0.5 to 2.0% by weight, more preferably 0.5 to 1.6% by weight.
  • the manganese (Mn) may be contained in an amount of more than 0 to 1.0 wt%
  • Manganese is a recrystallized nucleation site, which produces fine grains and then serves to inhibit grain growth and provide fine and uniform grains.
  • the magnesium alloy sheet which is another embodiment of the present invention to be described later,
  • the magnesium alloy sheet material may include cerium (Ce), for example, the cerium element may be contained singly or in the form of mi metal (mi schmet al). When included as micro metal, the mis-metal may further include rare earth elements such as La, Nd, Pr or a combination thereof.
  • the cerium may be contained in an amount of 0 to 0.5 wt% or less, preferably 0 to 0.2 wt% or less, based on the magnet alloy sheet material.
  • cerium above the above range is added, it is combined with magnesium and / or zinc to form a large amount of intermetallic compound and make it coarse, which may hinder rolling property, formability and corrosion resistance.
  • the anisotropy which is the difference in physical properties between the rolling direction RD and the plate material width direction TD, can be reduced.
  • the center segregation can be reduced as described above by controlling the alloy, its components, and the composition range. Specifically, it may be a result of controlling the composition and the composition range of the alloy so as to form the secondary phase (intermetallic compound) and the segregation to a minimum, and controlling the conditions to homogenization heat treatment and rolling (intermediate annealing).
  • the ratio of the thickness of the center segregation to the total thickness of the magnet alloy plate is 10% or less, it means that core segregation is hardly formed. Accordingly, when the center segregation in the magnet alloy plate material is in the above range, Anisotropy of the magneto-alloy plate material may be excellent.
  • anisotropy in the present specification means that the properties of the magnesium alloy sheet material are different depending on the orientation. Specifically, the rolling direction RD and the plate width
  • the anisotropy of the magnet alloy sheet material can be excellent. Also, in this specification, anisotropy
  • Excellentness means that the difference in physical properties between the rolling direction (RD) and the plate material width direction (TD) is small.
  • Intermetallic compound particles having an Mg-Ce-based secondary phase (intermetallic compound) of 0.5 pm to 20 / im, preferably Mg-Ce-based secondary phase (intermetallic compound) particles of 0. 5 to 5.
  • the magnesium alloy sheet according to an embodiment of the present invention may include Mn-based secondary phase particles having an average particle diameter of 1 m to 1 dish,
  • the magnesium alloy sheet material may include Mg-Ce, Mn, or a combination thereof. More specifically, the Mg-Ce system secondary phase may be a secondary phase containing Mg-Ce- (Zn) particles. On the other hand, the Mn-based secondary phase may be a secondary phase containing Mn- (Si) - (Fe) particles.
  • Mg-Ce-based second phase particles may be included from 1 to 30 per second area 100 ⁇ of the magnesium alloy plate.
  • At least one Mn-based secondary phase particle per 100 2 of the magnesium alloy sheet material may be included.
  • the moldability and corrosion resistance of the magnet alloy sheet material can be further improved.
  • the magnesium alloy sheet material includes crystal grains, and the average grain size of the crystal grains can be 2 to 15. [ The moldability and the strength are further improved in the above-mentioned range . In order to obtain the crystal grains of the above-mentioned sizes, it is necessary to precisely control the composition range of the additive element, the silver and the time of the homogenization heat treatment, the temperature at the time of warm rolling, and the rolling rate.
  • the limiting imposed 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 7 to 11 mm.
  • the threshold limit height is used as an index for evaluating the formability of the material, which means that the moldability of the material is improved as the height of the limit dome increases.
  • the above limited range is a marginal dome height which is significantly higher than a generally known magnesium alloy plate due to an increase in the grain boundary orientation distribution in the magnesium alloy sheet material. Accordingly, the magnesium alloy sheet material
  • the maximum gathering intensity may be 1 to 4 based on the [0001] plane.
  • the moldability of the magnesium alloy sheet material may be inferior.
  • the corrosion rate of the magnesium alloy sheet according to an embodiment of the present invention may be 2.0 mm / y or less. Specifically, it may be 1.5 mm / y or less. This may be a result of limiting the composition, the composition range and the relational expression of the magnesium alloy sheet described above. In addition, it can be a result of optimizing the homogenization heat treatment and rolling conditions after controlling the Fe content, especially the impurities.
  • the magneto-alloy plate material may have a critical bending radius value at room temperature of 4 R / t or less, preferably 3 R / t or less. Also,
  • the critical bending radius value at 200 degrees Celsius can be less than or equal to 1.5 R / t.
  • the difference in the critical bending radius value in the plate material width direction TD may be 0 to 0.5 or less. This means that the anisotropy of the magnesium alloy sheet material is excellent. As described above, the excellent anisotropy of the magnesium alloy sheet means that there is little difference in physical properties between the rolling direction and the sheet width direction.
  • the content of the additive element, the homogenization heat treatment condition, the rolling condition Is an effect that can be obtained by controlling the size and number of intermetallic compounds and the ratio of the two segregations of center segregation by optimization.
  • the thickness of the magnesium alloy sheet according to an embodiment of the present invention may be 0.1 to 5 mm.
  • the magnesium plate according to one embodiment of the present invention may be selected according to the properties required in the thickness range. However, the present invention is not limited thereto.
  • a method of manufacturing a magnesium alloy sheet according to another embodiment of the present invention is a method of manufacturing a magnesium alloy sheet material, wherein zinc (Zn) is contained in an amount of 0 to 2.0% by weight, manganese (Mn) (S100) of preparing a cast material by casting a molten alloy containing at least 0 wt% and 0.5 wt% or less of residual magnesium (Mg) and other unavoidable impurities; subjecting the cast material to a homogenization heat treatment (S200) Warm rolling the heat-treated cast material to prepare a rolled plate material (S300), and finally heat-treating the rolled plate material (S400).
  • zinc (Zn) is contained in an amount of 0 to 2.0% by weight, manganese (Mn) (S100) of preparing a cast material by casting a molten alloy containing at least 0 wt% and 0.5 wt% or less of residual magnesium (Mg) and other unavoidable impurities; subjecting the cast material to
  • the molten metal may satisfy the following relational expression (1).
  • [Zn], [Mn], and [Ce] refer to weight percent of each component.
  • the Fe content in the other brittle impurities contained in 100 wt% of the alloy molten metal as a whole may be 100 ppm or less.
  • the A1 content may be 0.3% by weight or less.
  • the kind of the impurity is not limited thereto, and may include other unavoidable impurities.
  • the alloy melt can be cast by gravity casting, continuous casting, strip casting (thin plate casting), sand casting, vacuum casting, centrifugal casting, die casting or chisel molding. Therefore, the alloy melt can be cast by gravity casting, continuous casting, strip casting (thin plate casting), sand casting, vacuum casting, centrifugal casting, die casting or chisel molding. Therefore,
  • the present invention is not limited thereto, and any method capable of producing a cast material is possible.
  • the steps (S200) to homogenization heat treatment to the cast material may be carried out 300 degrees (° C) to 500 in Figure (0 C). Further, the cast material is homogenized
  • the heat-treating step may be conducted for 1 to 30 hours.
  • the step (S200) of homogenizing the cast material may include a first homogenization heat treatment step (S210) and a second homogenization heat treatment step (S220).
  • the first homogenization heat treatment step (S210) is performed at a temperature of 300 ° C
  • the first homogenization heat treatment can be performed for 0.5 to 10 hours.
  • the second homogenization heat treatment step (S220) can be performed at 400 ° C ( 0 C) to 500 ° C ( 0 ° C).
  • secondary homogenization heat treatment can be performed for 0.5 to 20 hours.
  • the low melting point phase can be subjected to solution treatment by performing the first heat treatment step (S210) as described above.
  • the secondary heat treatment step (S220) as described above, the homogenization heat treatment can smoothly proceed. Therefore, by dividing the homogenization heat treatment step (S200) into two steps as described above, surface oxidation due to local melting on the low melting point can be prevented.
  • microstructure unevenness due to the superheating treatment can be prevented by homogenizing the casting material according to the temperature and time range, and the microstructure and segregation of the casting material can be sufficiently homogenized.
  • the steps of: preparing a plate material by rolling, warm rolling the homogenization heat treated cast material (S300) may be carried out 150 (° C) to 400 in Figure (0 C).
  • the cast material subjected to the homogenization heat treatment is subjected to heat treatment
  • the homogenized heat-treated cast material can be warm-rolled using a warm rolling mill.
  • intermediate annealing may be performed at least once between the warm rolling.
  • the intermediate annealing may be performed 300 degrees (0 C) to about 500 in FIG. (° C).
  • the intermediate annealing can be performed for 5 hours or less (excluding 0 hours). If the temperature and the time range are not satisfied, the stress of the hardened tissue is not sufficiently solved by the cumulative rolling reduction, and the annealing process may not be performed properly. Further, the abnormal crystal grains can grow due to excessive annealing.
  • the intermediate annealing can be performed at a cumulative reduction of 40% or more of the rolled plate material. More specifically, in the case of performing intermediate annealing when the cumulative rolling reduction is 40% or more, generation and growth of new non-bottoms recrystallized grains can be facilitated in the structure formed during rolling. Thereby contributing to improvement of moldability of the magnesium plate material.
  • the intermediate annealing execution rate may be 20% or less.
  • the intermediate annealing execution rate (number of intermediate annealing / total number of rolling) X 100 can be obtained.
  • the step S400 of performing the final heat treatment of the rolled plate may be performed at a temperature of 250 ° C to 500 ° C.
  • the step of final heat treatment of the rolled plate may be conducted for 5 hours or less (excluding 0 hours).
  • the final heat treatment temperature is less than 250 degrees Celsius ( 0 C)
  • the formation and dispersion of the non-bottoms recrystallized grains by recrystallization are insufficient, so that the formability due to the range of the present invention may not be satisfied.
  • the final heat treatment temperature is higher than 500 ° C ( 0 ° C)
  • surface oxidation may occur and it may not be possible to produce a perfect plate. Examples of the magnesium alloy sheet produced by the above-described method and
  • Examples and Comparative Examples were prepared with the components and compositions shown in Table 1 below. Concretely, a casting material was prepared by casting the alloy melt shown in Table 1 below. Then, the cast material was subjected to homogenization heat treatment for 1 to 30 hours at 300 ° C to 500 ° C ( 0 ° C). After the homogenization heat treatment process is completed,
  • intermediate annealing may be applied at least once.
  • the intermediate annealing process may be performed at a temperature between 300 [deg.] C and 500 [
  • the Erickson values, the V-bending test, and the salt precipitation test results of the above Examples and Comparative Examples were measured and are shown in Table 2 below.
  • the Ericsson figure shows the goodness of the formability
  • the V-bending test shows the goodness of formability and anisotropy
  • the corrosion property can be evaluated from the salt precipitation test.
  • the temperature of the die and the spherical punch is set to room temperature.
  • the outer peripheral portion of the plate material was fixed with a force of 10 kN, and then, using a spherical plate having a diameter of 20 mm, The plate was deformed. Thereafter, the punch was inserted until the plate material was broken, and then the deformation height of the plate material was measured at the time of breaking.
  • the deformation height of the plate measured in this manner is referred to as an Erickson value or
  • the V-bending test is performed as an index for measuring the degree of anisotropy of the formability, and the result is referred to as the limit bending radius (LBR).
  • the limit bending radius (LBR) value refers to the inner radius of curvature (R) of the plate after the bending test / the thickness (t) of the plate.
  • the prepared specimens were placed on a bending die having a length of 160 mm and a length of 80 mm, and the plate was placed at a rate of 20 mm / s at a speed of 20 mm / s using a bending punch having a lateral X-vertical size of 30 X 70 mm and an outer radius of curvature of 0 to 8R ° was bending.
  • the R value of the bending punch was varied while checking the presence or absence of a crack on the bending surface, and the crack was measured until no crack occurred.
  • the value of the limit bending radius (LBR) which is an index of bending anisotropy
  • the plate materials according to Examples and Comparative Examples were immersed in 1 liter of sodium chloride (NaCl) solution at room temperature for 3.5 hours, and then immersed in the following solution for 1 minute in order to remove oxides formed on the surface. More specifically, the oxide-coated plate was immersed in a solution containing 100 g of anhydrous chromic acid and 10 g of silver chromate in 1 liter of distilled water at 90 ° C to remove the surface oxide.
  • NaCl sodium chloride
  • the corrosion rate was calculated through the weight of the plate before oxide formation and the weight of plate after oxide removal. More specifically, the corrosion rate was determined by dividing the weight loss of the plate after oxide removal by the area of the specimen, Respectively.
  • Corrosion rate (initial weight of specimen - weight after removal of oxide) I (specimen area X density X salt precipitation time)
  • Examples 1 to 3 show that the Erickson value is 7 mm or more. More specifically, it can be seen that it is 8 mm or more. Also, the bend radius limit value at room temperature of 4 or less, limits the bending radius at 200 o C It is confirmed that the value is 1.5 or less. Further, it is confirmed that the anisotropy is excellent because the difference between the rolling direction (RD) and the plate bending radius (TD) is 0.5 or less, and the excellent corrosion resistance is also confirmed compared with Comparative Example 5 (AZ31) which is a commercial magnesium . Therefore, it was confirmed that the examples according to the present invention are excellent in both high corrosion resistance, room temperature moldability and anisotropy.
  • FIG. BRIEF DESCRIPTION OF THE DRAWINGS Fig. 1 is a photograph of a microstructure of the microstructure after (a) and (b) after homogenization heat treatment in Example 2 and Comparative Example 4 under an optical microscope.
  • FIG. 1 shows changes in microstructure with and without addition of Mn when the contents of Zn and Ce are the same. Specifically, as shown in FIG. 1, it can be confirmed that the microstructure of Example 2 is finer than that of Comparative Example 4 in (a) after homogenization heat treatment and (b) after final annealing.
  • FIG. 2 is a photograph of the composition analysis of each intermetallic compound analyzed by a scanning electron microscope (SEM) and a backscattered electron (BSE) image using SEM-EDS.
  • SEM scanning electron microscope
  • BSE backscattered electron
  • the intermetallic compound (1, 2) is an Mg- (Zn) -Ce intermetallic compound formed by the addition of Ce.
  • the intermetallic compound (3) is an Mn- (Si) - (Fe) intermetallic compound formed by the addition of Mn.
  • intermetallic compounds 1 and 2 magnesium There is a characteristic that the chemical potential difference with the base is not large. Accordingly, the intermetallic compounds 1 and 2 can reduce the galvanic corrosion due to the potential difference with the magnesium base.
  • Mg-Al intermetallic compounds generated from commercial magnesite alloys not containing Ce may cause galvanic corrosion due to the potential difference with the magnesium base.
  • the magnesium alloy sheet according to the embodiment of the present invention has a Fe content of less than lOOppm, and the corrosion rate may be less than 2mm / y.
  • the magneto-alloy plate according to the embodiment of the present invention can have an improved corrosion resistance and a corrosion rate of 2 mm / y or less.
  • each plate was heated to 90 degrees (° C)
  • Fig. 4 shows a comparison of the ⁇ 0001 ⁇ XRD pole figure of the embodiment and the comparative example.
  • the contour line according to the pole figuration is a stereo projection of the direction of the arbitrarily fixed crystal coordinate system in the specimen coordinate system. More specifically, the poles for the [0001] planes of the crystal grains of various orientations are displayed in the reference coordinate system, and the density contour lines are plotted according to the pole density distribution It is possible to show pole figure. At this time, the poles are fixed in a specific lattice direction by the Bragg angle, and a plurality of poles can be displayed for a single crystal. Therefore, the smaller the density distribution value of the contour line represented by the poling method is, the more the crystal grains of various orientations are distributed. The larger the density distribution value is
  • the maximum aggregate strength of the [0001] plane is the result of analyzing the crystal orientation of the magnesium alloy sheet by the above-described XRD analyzer.
  • the maximum density distribution value (aggregate intensity) of the [0001] plane in Examples 1 to 3 is a very small value of 4 or less.
  • the ⁇ 0001 ⁇ bottom surface organization is distributed much in RD and TD directions,
  • Comparative Example 1 it can be seen that the ⁇ 0001 ⁇ underside texture is not uniformly distributed in the RD and TD directions.
  • the comparative example contains much crystal grains of // C axis orientation compared to the embodiment, since the maximum set intensity value is large and the contour lines are dense. From this, it can be seen that the embodiment is more excellent in moldability than the comparative example.
  • the crystal orientation of grains can be measured not only by the pole figuration described above, but also by the EBSD image. More specifically, the EBSD can introduce electrons into a specimen through an electron beam and measure the crystal orientation of the crystal grains using inelastic scattering diffraction at the back of the specimen.
  • Example 2 the maximum set intensity value of Example 2 is very low as 2.79, while the maximum set intensity value of Comparative Example 5 is as high as 12.11. From this, it can be deduced that in Example 1, a large number of non-base texture tissues deviated from the orientation in the bottom-side texture structure are distributed As shown in the EBSD image, since the crystal grains of various colors are distributed in the second embodiment compared to the second comparative example, it can be seen that the texture of the underside is distributed widely. Specifically, in Comparative Example 5, it is visually confirmed that crystal grains (red) corresponding to the crystal orientation of the [C] -axis orientation are larger than those of Example 2.
  • FIG. 6 is a graph showing the results of V-bending test at room temperature (a) and 200 ° C (b) of Example 2, showing the microstructure of the RD (Rolling Diode) It is a photograph observed with an optical microscope.
  • the thickness ratio of the center segregation in Example 2 may be 10% or less.
  • the thickness ratio of the center segregation is 10% or less, so that anisotropy in the RD and TD directions can be excellent.
  • the aggregate intensities (peak intensities) of [0001] bases are 1 to 4, and thus microstructures having a large number of non-subsurface texture can be obtained. Also, it is possible to manufacture a magnesium alloy plate of high moldability and high corrosion resistance having a high room temperature Erickson value of 7 to 11 mm and a low corrosion rate of 2.0 mm / y or less.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Hard Magnetic Materials (AREA)

Abstract

La présente invention concerne une tôle d'alliage de magnésium et son procédé de fabrication. La tôle d'alliage de magnésium peut comporter, sur la base d'un total de 100 % en poids : du zinc (Zn) suivant une quantité supérieure à 0 et inférieure ou égale à 2,0 % en poids ; du manganèse (Mn) suivant une quantité supérieure à 0 et inférieure ou égale à 1,0 % en poids ; du cérium (Ce) suivant une quantité supérieure à 0 et inférieure ou égale à 0,5 % en poids ; et le complément de magnésium (Mg) et d'autres impuretés inévitables.
PCT/KR2018/008565 2017-08-03 2018-07-27 Tôle d'alliage de magnésium et son procédé de fabrication WO2019027188A1 (fr)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
KR20170098607 2017-08-03
KR10-2017-0098607 2017-08-03
KR10-2017-0180319 2017-12-26
KR1020170180319A KR102045063B1 (ko) 2017-08-03 2017-12-26 마그네슘 합금 판재 및 이의 제조방법

Publications (1)

Publication Number Publication Date
WO2019027188A1 true WO2019027188A1 (fr) 2019-02-07

Family

ID=65232789

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/KR2018/008565 WO2019027188A1 (fr) 2017-08-03 2018-07-27 Tôle d'alliage de magnésium et son procédé de fabrication

Country Status (1)

Country Link
WO (1) WO2019027188A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111304511A (zh) * 2020-03-27 2020-06-19 有研工程技术研究院有限公司 一种油气开采用镁合金材料及其制备方法和应用

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2008536005A (ja) * 2005-03-08 2008-09-04 ペ，ドン−ヒョン ミッシュメタルが添加されたマグネシウム合金、ミッシュメタルが添加されたマグネシウム合金加工材の製造方法及びこれによって製造されるマグネシウム合金加工材
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
KR20150065418A (ko) * 2013-12-05 2015-06-15 주식회사 포스코 마그네슘 합금 판재 및 이의 제조 방법
KR20150090380A (ko) * 2014-01-28 2015-08-06 순천대학교 산학협력단 성형성이 우수한 마그네슘 합금 및 그의 제조방법
KR101751521B1 (ko) * 2015-12-24 2017-06-27 주식회사 포스코 마그네슘 합금 판재 제조방법

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2008536005A (ja) * 2005-03-08 2008-09-04 ペ，ドン−ヒョン ミッシュメタルが添加されたマグネシウム合金、ミッシュメタルが添加されたマグネシウム合金加工材の製造方法及びこれによって製造されるマグネシウム合金加工材
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
KR20150065418A (ko) * 2013-12-05 2015-06-15 주식회사 포스코 마그네슘 합금 판재 및 이의 제조 방법
KR20150090380A (ko) * 2014-01-28 2015-08-06 순천대학교 산학협력단 성형성이 우수한 마그네슘 합금 및 그의 제조방법
KR101751521B1 (ko) * 2015-12-24 2017-06-27 주식회사 포스코 마그네슘 합금 판재 제조방법

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111304511A (zh) * 2020-03-27 2020-06-19 有研工程技术研究院有限公司 一种油气开采用镁合金材料及其制备方法和应用
CN111304511B (zh) * 2020-03-27 2022-01-04 有研工程技术研究院有限公司 一种油气开采用镁合金材料及其制备方法和应用

Similar Documents

Publication Publication Date Title
CN101550509B (zh) 烤漆固化性优良、室温时效得到抑制的铝合金板及其制造方法
TWI629369B (zh) 鋼板及鍍敷鋼板
JP6005544B2 (ja) 焼付け塗装硬化性に優れたアルミニウム合金板
JP5746528B2 (ja) 焼付け塗装硬化性に優れたアルミニウム合金板
JP5852534B2 (ja) 焼付け塗装硬化性に優れたアルミニウム合金板
CN108472699B (zh) 镁合金板材及其制造方法
JP5820315B2 (ja) 室温時効後のヘム加工性と焼付け塗装硬化性に優れたアルミニウム合金板
JP5985165B2 (ja) 焼付け塗装硬化性に優れたアルミニウム合金板
WO2019186930A1 (fr) Produit formé par estampage à chaud
US20200056270A1 (en) Highly molded magnesium alloy sheet and method for manufacturing same
WO2015034024A1 (fr) Plaque en alliage d'aluminium ayant d'excellentes propriétés de durcissement à la cuisson
KR20240042470A (ko) 열간 압연 강판
US20170349979A1 (en) Aluminum alloy sheet
TWI664302B (zh) Hot stamping
JP2022500565A (ja) マグネシウム合金板材およびその製造方法
WO2019027188A1 (fr) Tôle d'alliage de magnésium et son procédé de fabrication
JP2017210673A (ja) ｒ値の異方性が小さいプレス成形用アルミニウム合金板およびその製造方法
US20170349978A1 (en) Aluminum alloy sheet
KR102252289B1 (ko) 마그네슘 합금 판재 및 그 제조방법
KR102045063B1 (ko) 마그네슘 합금 판재 및 이의 제조방법
TWI663265B (zh) Hot stamping steel plate
JP5918187B2 (ja) 焼付け塗装硬化性に優れたアルミニウム合金板
JP6005613B2 (ja) 焼付け塗装硬化性に優れたアルミニウム合金板
TWI663267B (zh) Hot stamping
KR20240051972A (ko) 열간 압연 강판

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 18840498

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 18840498

Country of ref document: EP

Kind code of ref document: A1