WO2015126054A1 - Magnesium alloy board and preparation method therefor - Google Patents

Magnesium alloy board and preparation method therefor Download PDF

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Publication number
WO2015126054A1
WO2015126054A1 PCT/KR2014/013036 KR2014013036W WO2015126054A1 WO 2015126054 A1 WO2015126054 A1 WO 2015126054A1 KR 2014013036 W KR2014013036 W KR 2014013036W WO 2015126054 A1 WO2015126054 A1 WO 2015126054A1
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magnesium
weight
magnesium alloy
plate
less
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PCT/KR2014/013036
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French (fr)
Korean (ko)
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신광선
박상준
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서울대학교 산학협력단
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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
    • C22C23/02—Alloys based on magnesium with aluminium as the next major constituent
    • 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
    • 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
    • B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
    • B22D11/0622—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
    • B22D21/02—Casting exceedingly oxidisable non-ferrous metals, e.g. in inert atmosphere
    • B22D21/04—Casting aluminium or magnesium

Definitions

  • the present invention relates to a magnesium alloy sheet obtained by casting a magnesium alloy minimizes segregation generated in the strip casting process and a method of manufacturing the same. More specifically, the solidification section is controlled to be suitable for strip casting to minimize the segregation fraction of the sheet.
  • the present invention relates to a magnesium alloy sheet and a method for manufacturing the same, which can be implemented in comparison with AZ61, which is a commercial magnesium alloy, in which the mechanical properties thereof are not deteriorated or can be improved.
  • Magnesium alloy has the smallest density among structural materials, has excellent specific strength and inelastic coefficient, and has excellent absorbency against vibration, shock, electromagnetic waves, etc., and is considered to be a very suitable material for applications requiring lightweight materials.
  • the process of manufacturing parts using magnesium alloy includes gravity casting, die casting, extrusion, rolling and the like, and the manufacture of parts through a double die casting process accounts for more than 90%.
  • the strip casting process is a process of manufacturing a thin plate by directly supplying a molten metal between two rotating rolls.
  • the strip casting process has an advantage of cheaply manufacturing a magnesium alloy sheet, but depending on the composition and manufacturing conditions of the alloy, Inverse segregation and central segregation are generated inside the plate due to the distribution and roll reduction force, and this segregation adversely affects the surface state and the mechanical properties of the plate and causes the quality of the plate to degrade.
  • Mg-Al-Zn alloy system containing aluminum and zinc is mainly used for commercial strip casting magnesium alloy.
  • Zn which is a low melting point alloy element
  • the solidification section is wide, and a large amount of central segregation and reverse segregation is produced during casting. There is a limit to the use of.
  • Korean Laid-Open Patent Publication No. 2013-0043355 discloses a magnesium alloy sheet containing 1 to 3% by weight of Al and 0.5 to 3% by weight of Sn and minimizing central segregation and reverse segregation as a plate obtained through a strip casting process.
  • the tensile strength of the AT33 alloy added with the maximum content of Al and Sn is only 273-283 MPa, there is a difficulty in meeting the demand for high strength.
  • the present invention has been made to solve the problem of the center segregation and reverse segregation occurring during the strip casting of the commercial Mg-Al-Zn magnesium alloy, the selection of alloy elements and alloy elements that can minimize the solidification section of the alloy By controlling the content of, it is an object to provide a magnesium alloy sheet that can not only significantly suppress segregation generated during strip casting, but also obtain excellent mechanical properties.
  • Another object of the present invention to provide a method for producing the magnesium alloy sheet material.
  • the first aspect of the present invention for solving the above problems, Al: more than 3.0 ⁇ 10.0% by weight, the rest of the magnesium alloy consisting of magnesium and unavoidable impurities produced by a process including strip casting, sheet segregation It is to provide a magnesium alloy sheet having a fraction of 2.5% or less.
  • the second aspect of the present invention for solving the above problems, Al: more than 3.0 to 10.0% by weight and Sn: 0.1 to 6.0% by weight, the rest of the magnesium alloy consisting of magnesium and unavoidable impurities strip casting It is manufactured by the process containing, It is providing the magnesium alloy plate material whose segregation fraction of a plate material is 2.5% or less.
  • the third aspect of the present invention for solving the above problems, Al: more than 3.0 to 10.0% by weight and Mn: 0.1 to 3.0% by weight, the rest of the magnesium alloy consisting of magnesium and inevitable impurities strip casting It is manufactured by the process containing, It is providing the magnesium alloy plate material whose segregation fraction of a plate material is 2.5% or less.
  • the fourth aspect of the present invention for solving the above problems, Al: more than 3.0 to 10.0% by weight, Sn: 0.1 to 6.0% by weight and Ca: 0.1 to 5.0% by weight or misch metal: 0.1 to 5.0% by weight
  • the magnesium alloy sheet containing any one, and the rest is prepared by a process including strip casting of a magnesium alloy consisting of magnesium and unavoidable impurities, to provide a magnesium alloy sheet having a segregation fraction of the sheet of 2.5% or less.
  • the fifth aspect of the present invention for solving the above problems is Al: more than 3.0 to 10.0% by weight, Mn: 0.1 to 3.0% by weight, Ca: 0.1 to 5.0% by weight, and Ca: 0.1 to 5.0% by weight or Mish metal: any one of 0.1 to 5.0% by weight, the remainder of the magnesium alloy consisting of magnesium and the unavoidable impurities produced by a process including strip casting, providing a magnesium alloy sheet with a segregation fraction of the plate of 2.5% or less It is.
  • the segregation fraction may be 2.0% or less.
  • the misch metal may include one kind or a mixture of two or more elements belonging to atomic numbers 57 (La, lanthanum) to 71 (Lu, lutetium).
  • the misch metal may be cerium rich mismetal.
  • the content of Mn may be 0.1 to 0.3% by weight.
  • the content of Al may be 5.0 to 7.0% by weight.
  • the present invention (a) maintaining the molten magnesium alloy of any one of claims 1 to 5 at 650 ⁇ 750 °C and casting a plate through a strip casting process; (b) performing homogenization heat treatment of the cast plate at 200 to 500 ° C. for 0.5 to 48 hours; And (c) preheating the homogenized heat-treated plate to 200 to 500 ° C., heating the roll to 25 to 250 ° C., and performing hot rolling at a rolling reduction of 50% or less per pass so that the final rolling reduction is 90% or less. It provides a method for producing a magnesium alloy sheet comprising a; cold rolling or hot rolling step.
  • Magnesium alloy according to the present invention can effectively control the segregation when compared to the conventional commercial magnesium alloy AZ61 alloy when strip casting, it can exhibit better mechanical properties under the same rolling and heat treatment conditions .
  • the manufacturing method of the magnesium alloy according to the present invention can further improve the mechanical properties of the magnesium alloy.
  • 1A to 1B are graphs showing solidification sections according to compositions of an Mg-xAl-yZn-0.3Mn alloy system and an Mg-xAl-ySn-0.3Mn alloy system.
  • FIG. 2 is a schematic diagram of a strip casting apparatus for producing a strip cast sheet according to an embodiment of the present invention.
  • 3a to 3n is a microstructure photograph of the casting direction of the strip cast magnesium alloy according to an embodiment of the present invention.
  • the "plate segregation fraction” is the ratio of the area where the central segregation is formed among the cross-sectional areas of the sheet during strip casting, that is, the cross-sectional area with the central segregation divided by the total cross-sectional area of the sheet.
  • Mg-Al-Zn-based alloys mainly used for strip casting the solidification section is wide due to the influence of Zn, which is a low melting point alloy element, and thus a large amount of central segregation and inverse segregation is produced during casting, thereby limiting the utilization of plate materials. Attention is given to the study of magnesium alloys with excellent mechanical properties while minimizing central segregation and reverse segregation. Based on the Mg-Al alloy system, manganese (Mn), tin (Sn), calcium (Ca) or micrometals (Mm) When alloying elements such as) are added in consideration of the solidification section, it has been found that a plate member having excellent mechanical properties can be obtained while minimizing segregation generated in the strip casting process.
  • Mn manganese
  • Sn tin
  • Ca calcium
  • Mm micrometals
  • the reason for adding each component is as follows.
  • Al is an element exhibiting a solid solution effect, and when it is less than 3.0% by weight, it is difficult to expect an increase in strength, and when it exceeds 10.0% by weight, it promotes segregation due to precipitation of Mg 17 Al 12 phase, so 3.0 to 10.0% by weight It is preferable to be contained, and 5.0-7.0 weight% is more preferable.
  • Sn is a element that controls segregation generation because the solute distribution coefficient is relatively high compared to other elements such as Zn.
  • Sn is less than 0.1% by weight, the above effect cannot be obtained.
  • the solid solution is about 6.0% by weight, the addition of Sn in excess of the solid solution is likely to cause a large amount of central segregation, so the maximum amount of Sn is preferably limited to 6.0% by weight or less. It is preferable to contain.
  • Mn reacts with iron (Fe), which adversely affects the corrosion resistance of magnesium alloys, to form FeMn compounds, which are filtered by sludge to lower the Fe content of magnesium alloys, and thus improve the corrosion resistance of magnesium alloys. If it is less than the weight%, the above effects cannot be obtained. If it exceeds 3.0% by weight, the Al-Mn compound is more preferably contained at 0.1 to 3.0% by weight because it is crystallized at a high temperature.
  • Ca is an element that controls the texture and microstructure of the plate, and serves to improve the tensile strength and formability at room temperature.
  • Ca is less than 0.1% by weight, the above effect is hardly obtained. Since hot cracking occurs during casting or rolling by forming a 2 Ca phase or the like, it is preferably contained at 0.1 to 5.0% by weight.
  • Mish metal is an element that improves the formability of the sheet at room temperature, and when the content is less than 0.1% by weight, the above effect is hardly obtained, and when the content exceeds 5.0% by weight, the casting temperature is increased due to the high temperature crystallized phase. It is preferable to contain at -5.0 weight%.
  • the mismetal may generally use one kind or a mixture of two or more kinds of elements belonging to atomic numbers 57 (La, lanthanum) to 71 (Lu, lutetium), and cerium rich mismetal (Mm) may be approximately 50% by weight.
  • the magnesium alloy sheet according to the present invention comprises the steps of (a) maintaining the molten magnesium alloy of any one of claims 1 to 5 at 650 ⁇ 750 °C and casting the sheet through a strip casting process; (b) performing homogenization heat treatment of the cast plate at 200 to 500 ° C. for 0.5 to 48 hours, and (c) preheating the homogenized heat treatment plate to 200 to 500 ° C., and heating the roll to 25 to 250 ° C. After the hot rolling is carried out at a rolling reduction of 50% or less per pass, it may be manufactured by performing cold rolling or hot rolling so that the final rolling reduction is 90% or less.
  • the temperature of the molten metal is less than 650 ° C.
  • the reduction in rolling pressure during casting increases considerably, and the segregation is increased.
  • the melting temperature is higher than 750 ° C., solidification is delayed when strip casting, and thus, a normal plate cannot be manufactured. It is preferable to keep it at 750 degreeC.
  • the rotating roll speed is maintained at 1 to 10 m / min so that the cooling rate of the molten metal is 10 2 to 10 3 K / s when the molten metal escapes between the rolls.
  • the center segregation fraction of the alloy sheet produced by the strip casting process is less than 2.5%, and if it exceeds 2.5%, the surface quality is adversely affected by the volume change and remelting in the process of the segregation in the homogenization heat treatment process. Since it is crazy, it is preferable to keep the central segregation fraction of the alloy sheet as less than 2.5%.
  • the homogenization heat treatment temperature is less than 300 °C, the time required for heat treatment is considerably long, and when it exceeds 500 °C, the homogenization heat treatment temperature is 300-500 degreeC is preferable, and when a homogenization heat processing time is less than 30 minutes, a homogenization effect cannot be achieved, and when it exceeds 48 hours, 30 minutes-48 hours are preferable because a crystal grain coarsens.
  • the plate material subjected to the homogenization heat treatment can be rolled to improve the sheet production and mechanical properties, wherein the hot rolling occurs significantly when the heating temperature of the rolling roll is less than 25 °C, 250 °C When exceeding, since the phenomenon which a board
  • the heating temperature of the plate is less than 200 °C the generation of edge cracks in the plate significantly increases, and if it exceeds 500 °C partially because the remelting occurs in the plate is preferably the heating temperature of the plate is 200 ⁇ 500 °C.
  • the inventors derived [Formula 1] and [Formula 2] for estimating the liquidus temperature and the solidus temperature of the alloy by composition, using the Pandat program, which is a thermodynamic simulation program, and based on the size of the solidification section of each alloy was predicted.
  • Liquidus Temperature (° C) 650.00-5.16Al-1.33Sn-3.04Zn + 0.39Mn-0.12SnAl-0.06ZnSn-0.10ZnAl-0.03MnSn-0.07MnAl-0.03MnZn (where Al, Sn, Zn and Mn are these elements) Weight percent of
  • Solidus temperature (° C) 650.00-18.51Al-5.44Sn-37.89Zn + 0.35Mn-0.54SnAl-1.61ZnSn + 1.65ZnAl-0.2Zn 2 Al-0.26MnSn + 1.33MnSn + 1.33MnAl + 1.23MnZn (where Al , Sn, Zn and Mn are the weight percent of these elements)
  • 1A to 1B illustrate solidification intervals according to the composition of the Mg-xAl-yZn-0.3Mn alloy system and the Mg-xAl-ySn-0.3Mn alloy system from the liquidus and solidus lines derived from Equations 1 and 2; The graph shown.
  • the alloy composition of Table 2 is selected in consideration of the size of the solidification section and the effect on the mechanical properties of the magnesium alloy when added, and in Table 2, No. 2, No. 3 and No. 14 alloys. Is for comparison with an alloy according to an embodiment of the invention.
  • the strip casting apparatus includes a twin roll 10 made of a Cu-Be alloy, a crucible 20 accommodating molten metal, a nozzle 30 for injecting molten metal from the crucible 20 to the pair roll 10, and And a pendulum 40 disposed in the crucible 20 to direct the molten metal to the nozzle and a hot chamber 50 to receive the crucible and maintain the temperature at a predetermined temperature or higher.
  • the diameter of the roll is 140mm.
  • the alloy prepared as shown in Table 1 was prepared by applying a melt temperature of 700 ⁇ 720 °C, roll speed 3 ⁇ 4mpm, roll gap 2mm conditions.
  • specimens were taken in the transverse direction from the sheet produced by the strip casting process, and each specimen was subjected to mechanical polishing using sandpaper up to 4000 times, followed by 0.05 mm alumina. The final fine polishing was performed using the powder. The polished specimens were etched with 0.5% nital solution and then microstructures were observed using an optical microscope.
  • FIG. 3A is a microstructure photograph of Example No. 1 strip cast sheet observed in the casting direction.
  • Figure 3 it can be seen that segregation was generated in the center of the plate, which is the final solidified portion of the Zn-added AZ60 and AZ61 alloy, the plate segregation was found to be 3.30% and 2.66%, respectively. This is because solute atoms of Al and Zn having a partition coefficient of less than 1 are redistributed from the surface of the sheet.
  • an alloy system containing Zn which is a low melting point alloy element, has a low solidus temperature even when a small amount is added, thereby generating a relatively large amount of central segregation and is not suitable for the strip casting process.
  • Table 3 shows the central segregation fraction of the plate strip cast with magnesium alloy according to the Examples and Comparative Examples of the present invention, the fraction of the central segregation was calculated using ImageJ, an image analysis program, the area and the area of the central segregation The total area of is taken into account.
  • the central segregation fraction is generated less than the Mg-6Al-xZn alloy.
  • the central segregation fraction of the AT67 alloy was 6.20%, which was higher than that of the Mg-6Al-xZn alloy, and the Sn alloying element included 7.0 weights because the Sn solid solution of the magnesium alloy containing 6.0 weights of Al alloys was about 6.0 weights.
  • the AT67 alloy it can be seen that a relatively large amount of central segregation is generated.
  • the homogenization heat treatment was carried out at 400 ° C. for 12 hours.
  • the homogenized heat-treated plate was preheated to 350 ° C. and then hot rolled at a rolling rate of 15% in a rolling roll heated to 200 ° C.
  • the tensile strength of the commercial alloy AZ61 alloy is 301.5MPa, alloys according to the embodiment of the present invention as compared to the AZ61 alloy as described above, while the lower the center segregation as described above, the implementation of tensile strength of 285MPa or more
  • the tensile strengths of 302.5 MPa and 318.2 MPa were found to be better than those of the AZ61 alloy.

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Abstract

The purpose of the present invention is to provide a strip cast magnesium alloy board, wherein the solidification range of a magnesium alloy is controlled by adding, on the basis of a Mg-Al alloy system, an alloy element such as manganese (Mn), tin (Sn), calcium (Ca) or misch metal (Mm), thereby controlling the segregation fraction generated in a strip casting process, and thus the magnesium alloy board has excellent mechanical properties compared with a conventional magnesium alloy board. A magnesium alloy board for strip casting according to the present invention is a Mg-Al-Mn-X (X= Ca or RE) alloy system comprising Al in an amount of more than 3.0 wt% and less than or equal to 10.0 wt% and 0.1-3.0 wt% of Mn, and comprising 0.1-5.0 wt% of Ca or 0.1-5.0 wt% of a rare earth metal and the balance of magnesium and inevitable impurities, and a Mg-Al-Sn-X (X=Ca or RE) alloy system comprising Al of 3.0-10.0 wt%, 0.1-6.0 wt% of Sn and 0.1-0.3 wt% of Mn, and comprising 0.1-5.0 wt% of Ca or 0.1-5.0 wt% of a rare earth metal and the balance of magnesium and inevitable impurities, and thus the segregation fraction of the board is less than or equal to 2.5%.

Description

마그네슘 합금 판재 및 이의 제조방법Magnesium alloy sheet and its manufacturing method
본 발명은 스트립 캐스팅 공정에서 발생하는 편석을 최소화한 마그네슘 합금을 캐스팅하여 얻은 마그네슘 합금 판재와 이의 제조방법에 관한 것으로, 보다 상세하게는 스트립 캐스팅에 적합하도록 응고 구간이 제어되어 판재의 편석분율을 최소화할 수 있고, 상용 마그네슘 합금인 AZ61과 대비하여, 그 기계적 특성이 저하되지 않거나 향상될 수 있어 우수한 기계적 특성을 구현할 수 있는 마그네슘 합금 판재와 이의 제조방법에 관한 것이다.The present invention relates to a magnesium alloy sheet obtained by casting a magnesium alloy minimizes segregation generated in the strip casting process and a method of manufacturing the same. More specifically, the solidification section is controlled to be suitable for strip casting to minimize the segregation fraction of the sheet. The present invention relates to a magnesium alloy sheet and a method for manufacturing the same, which can be implemented in comparison with AZ61, which is a commercial magnesium alloy, in which the mechanical properties thereof are not deteriorated or can be improved.
마그네슘 합금은 구조용 재료 중에서 최소의 밀도를 갖고 있는 동시에 우수한 비강도와 비탄성계수를 갖고 있으며, 진동, 충격, 전자파 등에 대한 흡수성이 탁월하여 경량화 소재가 요구되는 분야에 매우 적합한 소재로 평가받고 있다.Magnesium alloy has the smallest density among structural materials, has excellent specific strength and inelastic coefficient, and has excellent absorbency against vibration, shock, electromagnetic waves, etc., and is considered to be a very suitable material for applications requiring lightweight materials.
현재 마그네슘 합금을 이용하여 부품을 제조하는 공정으로는 중력주조, 다이캐스팅, 압출, 압연 등이 있으며, 이중 다이캐스팅 공정을 통한 부품의 제조가 90%이상을 차지하고 있다. 하지만 우수한 기계적 특성과 기존의 방법에 비해 보다 효율적인 제조가 가능한 스트립 캐스팅 공정이 주목받고 있다.Currently, the process of manufacturing parts using magnesium alloy includes gravity casting, die casting, extrusion, rolling and the like, and the manufacture of parts through a double die casting process accounts for more than 90%. However, attention has been paid to strip casting processes, which have excellent mechanical properties and are more efficient than conventional methods.
스트립 캐스팅 공정은 회전하는 양 롤 사이에 용탕을 직접 공급하여 박판을 제조하는 공정으로써 마그네슘 합금 판재를 저렴하게 제조할 수 있는 장점을 지니고 있으나, 합금의 조성 및 제조 조건에 따라 응고 과정 중 용질 원자의 분배 및 롤 압하력에 의해 판재 내부에 역편석 및 중심편석이 발생하며, 이러한 편석은 판재의 표면 상태 및 기계적 특성에 악영향을 미쳐 판재의 품질을 저하시키는 원인이 된다.The strip casting process is a process of manufacturing a thin plate by directly supplying a molten metal between two rotating rolls. However, the strip casting process has an advantage of cheaply manufacturing a magnesium alloy sheet, but depending on the composition and manufacturing conditions of the alloy, Inverse segregation and central segregation are generated inside the plate due to the distribution and roll reduction force, and this segregation adversely affects the surface state and the mechanical properties of the plate and causes the quality of the plate to degrade.
최근 상업적으로 사용되고 있는 스트립 캐스팅용 마그네슘 합금은 알루미늄과 아연이 들어간 Mg-Al-Zn합금계가 주로 사용되고 있으나 저융점 합금원소인 Zn의 영향으로 응고 구간이 넓어 주조 시 중심편석 및 역편석이 다량 생성하여 판재의 활용에 한계가 있다.Mg-Al-Zn alloy system containing aluminum and zinc is mainly used for commercial strip casting magnesium alloy. However, due to Zn, which is a low melting point alloy element, the solidification section is wide, and a large amount of central segregation and reverse segregation is produced during casting. There is a limit to the use of.
한편, 한국공개특허공보 제2013-0043355호에는 Al: 1~3중량%와 Sn 0.5~3중량%를 포함하고 스트립 캐스팅 공정을 통해 얻어진 판재로서 중심편석과 역편석을 최소화한 마그네슘 합금 판재가 개시되어 있는데, Al과 Sn의 최대 함량으로 첨가된 AT33합금의 인장강도는 273~283MPa에 불과하여, 이에 비해 고강도가 요구되는 수요에는 대응하기 어려운 점이 있다.Meanwhile, Korean Laid-Open Patent Publication No. 2013-0043355 discloses a magnesium alloy sheet containing 1 to 3% by weight of Al and 0.5 to 3% by weight of Sn and minimizing central segregation and reverse segregation as a plate obtained through a strip casting process. Although the tensile strength of the AT33 alloy added with the maximum content of Al and Sn is only 273-283 MPa, there is a difficulty in meeting the demand for high strength.
본 발명은 상기 상용의 Mg-Al-Zn 마그네슘 합금의 스트립 캐스팅 시 발생하는 중심편석 및 역편석의 문제를 해결하기 위해 안출된 것으로서, 합금의 응고구간을 최소화할 수 있는 합금원소의 선정과 그 합금원소의 함량을 제어함으로써, 스트립 캐스팅 시 발생하는 편석을 크게 억제할 수 있을 뿐 아니라, 우수한 기계적 특성을 얻을 수 있는 마그네슘 합금 판재를 제공하는 것을 과제로 한다.The present invention has been made to solve the problem of the center segregation and reverse segregation occurring during the strip casting of the commercial Mg-Al-Zn magnesium alloy, the selection of alloy elements and alloy elements that can minimize the solidification section of the alloy By controlling the content of, it is an object to provide a magnesium alloy sheet that can not only significantly suppress segregation generated during strip casting, but also obtain excellent mechanical properties.
본 발명의 다른 과제는 상기 마그네슘 합금 판재의 제조방법을 제공하는데 있다.Another object of the present invention to provide a method for producing the magnesium alloy sheet material.
상기 과제를 해결하기 위한 본 발명의 제1측면은, Al:3.0초과~10.0중량%를 함유하고, 나머지는 마그네슘과 불가피한 불순물로 이루어진 마그네슘 합금을 스트립 캐스팅을 포함하는 공정으로 제조한 것으로, 판재 편석 분율이 2.5%이하인 마그네슘 합금 판재를 제공하는 것이다.The first aspect of the present invention for solving the above problems, Al: more than 3.0 ~ 10.0% by weight, the rest of the magnesium alloy consisting of magnesium and unavoidable impurities produced by a process including strip casting, sheet segregation It is to provide a magnesium alloy sheet having a fraction of 2.5% or less.
또한, 상기 과제를 해결하기 위한 본 발명의 제2측면은, Al:3.0초과~10.0중량%와 Sn:0.1~6.0중량%를 함유하고, 나머지는 마그네슘과 불가피한 불순물로 이루어진 마그네슘 합금을 스트립 캐스팅을 포함하는 공정으로 제조한 것으로, 판재의 편석 분율이 2.5%이하인 마그네슘 합금 판재를 제공하는 것이다.In addition, the second aspect of the present invention for solving the above problems, Al: more than 3.0 to 10.0% by weight and Sn: 0.1 to 6.0% by weight, the rest of the magnesium alloy consisting of magnesium and unavoidable impurities strip casting It is manufactured by the process containing, It is providing the magnesium alloy plate material whose segregation fraction of a plate material is 2.5% or less.
또한, 상기 과제를 해결하기 위한 본 발명의 제3측면은, Al:3.0초과~10.0중량%와 Mn:0.1~3.0중량%를 함유하고, 나머지는 마그네슘과 불가피한 불순물로 이루어진 마그네슘 합금을 스트립 캐스팅을 포함하는 공정으로 제조한 것으로, 판재의 편석 분율이 2.5%이하인 마그네슘 합금 판재를 제공하는 것이다.In addition, the third aspect of the present invention for solving the above problems, Al: more than 3.0 to 10.0% by weight and Mn: 0.1 to 3.0% by weight, the rest of the magnesium alloy consisting of magnesium and inevitable impurities strip casting It is manufactured by the process containing, It is providing the magnesium alloy plate material whose segregation fraction of a plate material is 2.5% or less.
또한, 상기 과제를 해결하기 위한 본 발명의 제4측면은, Al:3.0초과~10.0중량%, Sn:0.1~6.0중량% 및 Ca:0.1~5.0중량% 또는 미쉬메탈:0.1~5.0중량% 중 어느 하나를 함유하고, 나머지는 마그네슘과 불가피한 불순물로 이루어진 마그네슘 합금을 스트립 캐스팅을 포함하는 공정으로 제조한 것으로, 판재의 편석 분율이 2.5%이하인 마그네슘 합금 판재를 제공하는 것이다.In addition, the fourth aspect of the present invention for solving the above problems, Al: more than 3.0 to 10.0% by weight, Sn: 0.1 to 6.0% by weight and Ca: 0.1 to 5.0% by weight or misch metal: 0.1 to 5.0% by weight The magnesium alloy sheet containing any one, and the rest is prepared by a process including strip casting of a magnesium alloy consisting of magnesium and unavoidable impurities, to provide a magnesium alloy sheet having a segregation fraction of the sheet of 2.5% or less.
또한, 상기 과제를 해결하기 위한 본 발명의 제5측면은, Al:3.0초과~10.0중량%, Mn:0.1~3.0중량%, Ca:0.1~5.0중량%, 및 Ca:0.1~5.0중량% 또는 미쉬메탈:0.1~5.0중량% 중 어느 하나를 함유하며, 나머지는 마그네슘과 불가피한 불순물로 이루어진 마그네슘 합금을 스트립 캐스팅을 포함하는 공정으로 제조한 것으로, 판재의 편석 분율이 2.5%이하인 마그네슘 합금 판재를 제공하는 것이다.In addition, the fifth aspect of the present invention for solving the above problems is Al: more than 3.0 to 10.0% by weight, Mn: 0.1 to 3.0% by weight, Ca: 0.1 to 5.0% by weight, and Ca: 0.1 to 5.0% by weight or Mish metal: any one of 0.1 to 5.0% by weight, the remainder of the magnesium alloy consisting of magnesium and the unavoidable impurities produced by a process including strip casting, providing a magnesium alloy sheet with a segregation fraction of the plate of 2.5% or less It is.
본 발명의 제1측면 내지 제5측면에 있어서, 상기 편석분율은 2.0% 이하일 수 있다.In the first to fifth aspects of the present invention, the segregation fraction may be 2.0% or less.
본 발명의 제4측면 또는 제5측면에 있어서, 상기 미쉬메탈은 원자번호 57(La, 란탄) 내지 71(Lu, 루테튬)에 속하는 원소의 1종 또는 2종 이상의 혼합물을 포함할 수 있다.In the fourth or fifth aspect of the present invention, the misch metal may include one kind or a mixture of two or more elements belonging to atomic numbers 57 (La, lanthanum) to 71 (Lu, lutetium).
본 발명의 제4측면 또는 제5측면에 있어서, 상기 미쉬메탈은 세륨리치 미시메탈일 수 있다.In the fourth or fifth aspect of the present invention, the misch metal may be cerium rich mismetal.
본 발명의 제3측면 또는 제5측면에 있어서, 상기 Mn의 함량은 0.1~0.3중량%일 수 있다.In the third or fifth aspect of the present invention, the content of Mn may be 0.1 to 0.3% by weight.
본 발명의 제1측면 내지 제5측면에 있어서, 상기 Al의 함량은 5.0~7.0중량%일 수 있다.In the first to fifth aspects of the present invention, the content of Al may be 5.0 to 7.0% by weight.
상기 다른 과제를 해결하기 위해 본 발명은, (a) 제1항 내지 제5항 중 어느 한 항에 기재된 마그네슘 합금의 용탕을 650~750℃로 유지하고 스트립 캐스팅 공정을 통해 판재를 주조하는 단계; (b) 주조된 판재를 200~500℃에서 0.5~48시간 동안 균질화 열처리를 실시하는 단계; 및 (c) 균질화 열처리된 판재를 200~500℃로 예열하고, 롤을 25~250℃로 가열한 후 1패스당 50% 이하의 압하율로 열간 압연을 실시하여 최종 압하량이 90% 이하가 되도록 냉간 압연 또는 열간 압연을 실시하는 단계;를 포함하는 마그네슘 합금 판재의 제조방법을 제공한다.In order to solve the above another problem, the present invention, (a) maintaining the molten magnesium alloy of any one of claims 1 to 5 at 650 ~ 750 ℃ and casting a plate through a strip casting process; (b) performing homogenization heat treatment of the cast plate at 200 to 500 ° C. for 0.5 to 48 hours; And (c) preheating the homogenized heat-treated plate to 200 to 500 ° C., heating the roll to 25 to 250 ° C., and performing hot rolling at a rolling reduction of 50% or less per pass so that the final rolling reduction is 90% or less. It provides a method for producing a magnesium alloy sheet comprising a; cold rolling or hot rolling step.
본 발명에 따른 마그네슘 합금은 스트립 캐스팅을 수행하였을 때, 기존의 상용 마그네슘 합금인 AZ61 합금에 비해 편석이 생기는 것을 효과적으로 제어할 수 있고, 동일한 조건의 압연 및 열처리 조건에서 보다 우수한 기계적 특성을 나타낼 수 있다.Magnesium alloy according to the present invention can effectively control the segregation when compared to the conventional commercial magnesium alloy AZ61 alloy when strip casting, it can exhibit better mechanical properties under the same rolling and heat treatment conditions .
또한, 본 발명에 따른 마그네슘 합금의 제조방법은 마그네슘 합금의 기계적 특성을 보다 향상시킬 수 있다.In addition, the manufacturing method of the magnesium alloy according to the present invention can further improve the mechanical properties of the magnesium alloy.
도 1a~도 1b는 Mg-xAl-yZn-0.3Mn 합금계와 Mg-xAl-ySn-0.3Mn 합금계의 조성에 따른 응고 구간을 나타낸 그래프이다.1A to 1B are graphs showing solidification sections according to compositions of an Mg-xAl-yZn-0.3Mn alloy system and an Mg-xAl-ySn-0.3Mn alloy system.
도 2는 본 발명의 실시예에 따른 스트립 캐스트 판재를 제조하기 위한 스트립 캐스팅 장치의 모식도이다.2 is a schematic diagram of a strip casting apparatus for producing a strip cast sheet according to an embodiment of the present invention.
도 3a~도 3n은 본 발명의 실시예에 따른 스트립 캐스트 마그네슘 합금의 주조방향에 대한 미세조직사진이다.3a to 3n is a microstructure photograph of the casting direction of the strip cast magnesium alloy according to an embodiment of the present invention.
본 발명의 실시예들을 설명하기 위해 사용되는 단수 형태들은 문구들이 이와 명백히 반대의 의미를 나타내지 않는 한 복수 형태들도 포함하는 의미이다. 그리고 '포함한다'의 의미는 특정 특성, 영역, 정수, 단계, 동작, 요소 및 /또는 성분을 구체화하며 다른 특정 특성, 영역, 정수, 단계, 동작, 요소, 성분 및/또는 군의 존재나 부가를 제외하는 것은 아니다.The singular forms used to describe the embodiments of the present invention are intended to include the plural forms as well, unless the phrases clearly indicate the opposite. And “includes” embodies a particular property, region, integer, step, operation, element, and / or component, and the presence or addition of another particular property, region, integer, step, operation, element, component, and / or group. It is not excluded.
다르게 정의하지는 않았지만 여기에 사용되는 기술용어 및 과학 용어를 포함하는 모든 용어들은 본 발명이 속하는 기술분야에서 통상의 지식을 가진 자가 일반적으로 이해하는 의미와 동일한 의미이다. 또한, 보통 사용되는 사전에 정의된 용어들은 관련 기술 문헌과 현재 개시된 내용에 부합되는 사전에 정의된 용어들은 관련 기술 문헌과 현재 개시된 내용에 부합하는 의미를 갖는 것으로 추가 해석되고 정의되지 않는 한 이상적이거나 매우 공식적인 의미로 해석되지 않는다.Unless defined otherwise, all terms including technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art. In addition, the commonly used terms defined in advance are ideal unless they are additionally interpreted and defined as having a meaning consistent with the related technical literature and the presently disclosed contents. It is not interpreted in a very official sense.
이하 첨부된 도면들을 참조하여 마그네슘 합금 판재의 제조방법 및 이를 이용하여 제조된 마그네슘 합금 판재에 대한 실시예들을 상세하게 설명하겠지만 본 발명이 하기의 실시예들에 제한되는 것은 아니다. 따라서 해당 분야에서 통상의 지식을 가진 자라면 본 발명의 기술적 사상을 벗어나지 않는 범위 내에서 본 발명을 다양하게 변경할 수 있음은 자명하다.Hereinafter, with reference to the accompanying drawings will be described in detail an embodiment of a method for producing a magnesium alloy plate and a magnesium alloy plate manufactured using the same, but the present invention is not limited to the following embodiments. Therefore, it will be apparent to those skilled in the art that the present invention may be variously modified without departing from the technical spirit of the present invention.
본 발명에 있어서, "판재 편석 분율"이란 스트립 캐스팅 시 판재의 단면적 중에서 중심 편석이 형성된 면적의 비율, 즉 중심편석이 있는 단면적을 판재의 전체 단면적으로 나눈 값이다.In the present invention, the "plate segregation fraction" is the ratio of the area where the central segregation is formed among the cross-sectional areas of the sheet during strip casting, that is, the cross-sectional area with the central segregation divided by the total cross-sectional area of the sheet.
본 발명자들은 스트립 캐스팅에 주로 사용되고 있는 Mg-Al-Zn계 합금의 경우, 저융점 합금원소인 Zn의 영향으로 응고 구간이 넓어 주조 시 중심편석 및 역편석이 다량 생성하여 판재의 활용에 한계가 있음에 주목하고, 중심편석 및 역편석을 최소화하면서 기계적 특성이 우수한 마그네슘 합금에 대해 연구한 결과, Mg-Al 합금계를 기본으로 망간(Mn), 주석(Sn), 칼슘(Ca) 또는 미시메탈(Mm) 등의 합금원소를 응고 구간을 고려하여 첨가할 경우, 스트립 캐스팅 공정에서 발생하는 편석을 최소화함과 동시에 우수한 기계적 특성을 지닌 판재를 얻을 수 있음을 밝혀내고 본 발명에 이르게 되었다.In the case of Mg-Al-Zn-based alloys mainly used for strip casting, the solidification section is wide due to the influence of Zn, which is a low melting point alloy element, and thus a large amount of central segregation and inverse segregation is produced during casting, thereby limiting the utilization of plate materials. Attention is given to the study of magnesium alloys with excellent mechanical properties while minimizing central segregation and reverse segregation. Based on the Mg-Al alloy system, manganese (Mn), tin (Sn), calcium (Ca) or micrometals (Mm) When alloying elements such as) are added in consideration of the solidification section, it has been found that a plate member having excellent mechanical properties can be obtained while minimizing segregation generated in the strip casting process.
본 발명에 따른 상기 제1 내지 제5 측면에 따른 마그네슘 합금 판재에 있어서, 각 성분의 첨가 이유는 다음과 같다.In the magnesium alloy sheet according to the first to fifth aspects according to the present invention, the reason for adding each component is as follows.
Al은 고용강화 효과를 나타는 원소로써, 3.0중량% 미만일 경우 강도 증가 현상을 기대하기 힘들고, 10.0중량%를 초과할 경우 Mg17Al12상 석출로 인해 편석 형성을 촉진하므로, 3.0~10.0중량%으로 함유되는 것이 바람직하며, 5.0~7.0중량%가 보다 바람직하다.Al is an element exhibiting a solid solution effect, and when it is less than 3.0% by weight, it is difficult to expect an increase in strength, and when it exceeds 10.0% by weight, it promotes segregation due to precipitation of Mg 17 Al 12 phase, so 3.0 to 10.0% by weight It is preferable to be contained, and 5.0-7.0 weight% is more preferable.
Sn은 상대적으로 Zn등 다른 원소와 비교해 볼 때, 용질분배계수가 상대적으로 높아 편석 발생을 제어하는 원소로써, 0.1중량% 미만일 경우 상기의 효과를 얻을 수 없으며, Al이 포함된 마그네슘 합금에서 Sn의 고용한이 대략 6.0중량%이기 때문에 고용한을 초과하여 Sn을 첨가할 경우 다량의 중심 편석이 발생할 가능성이 높아 최대 Sn의 첨가량을 6.0중량%이하로 제한되는 것이 바람직하므로, 0.1~6.0중량%으로 함유되는 것이 바람직하다.Sn is a element that controls segregation generation because the solute distribution coefficient is relatively high compared to other elements such as Zn. When Sn is less than 0.1% by weight, the above effect cannot be obtained. Since the solid solution is about 6.0% by weight, the addition of Sn in excess of the solid solution is likely to cause a large amount of central segregation, so the maximum amount of Sn is preferably limited to 6.0% by weight or less. It is preferable to contain.
Mn은 마그네슘합금의 내식성에 악영향을 미치는 철(Fe)과 반응하여 FeMn화합물을 형성하고 이 화합물은 슬러지로 걸러져 마그네슘합금의 Fe 함량을 낮추기 때문에 마그네슘합금의 내식성을 개선하는 역할을 하는 원소로써, 0.1중량% 미만일 경우 상기의 효과를 얻을 수 없으며, 3.0중량%를 초과할 경우 Al-Mn화합물의 고온에서 정출하기때문에 0.1~3.0중량%으로 함유되는 것이 보다 바람직하다.Mn reacts with iron (Fe), which adversely affects the corrosion resistance of magnesium alloys, to form FeMn compounds, which are filtered by sludge to lower the Fe content of magnesium alloys, and thus improve the corrosion resistance of magnesium alloys. If it is less than the weight%, the above effects cannot be obtained. If it exceeds 3.0% by weight, the Al-Mn compound is more preferably contained at 0.1 to 3.0% by weight because it is crystallized at a high temperature.
Ca은 판재의 집합조직 및 미세조직을 제어하는 원소로써, 상온 인장강도와 성형성을 향상시키는 역할을 하며, 0.1중량% 미만일 경우 상기의 효과는 거의 얻을 수 없으며, 5.0중량%를 초과할 경우 Al2Ca상 등을 형성하여 주조 또는 압연 시 Hot Cracking를 발생하기 때문에, 0.1~5.0중량%으로 함유되는 것이 바람직하다.Ca is an element that controls the texture and microstructure of the plate, and serves to improve the tensile strength and formability at room temperature. When Ca is less than 0.1% by weight, the above effect is hardly obtained. Since hot cracking occurs during casting or rolling by forming a 2 Ca phase or the like, it is preferably contained at 0.1 to 5.0% by weight.
미쉬메탈(Mm)은 판재의 상온 성형성을 향상시키는 원소로써, 0.1중량% 미만일 경우 상기의 효과를 거의 얻을 수 없으며, 5.0중량%를 초과할 경우 고온 정출상으로 인해 주조 온도를 증가시키므로, 0.1~5.0중량%으로 함유되는 것이 바람직하다. 상기 미쉬메탈은 일반적으로 원자번호 57(La, 란탄) 내지 71(Lu, 루테튬)에 속하는 원소의 1종 또는 2종 이상의 혼합물을 사용할 수 있으며, 세륨리치 미시메탈(Mm)은 대략 50 중량%의 Ce(세륨), 25 중량%의 La(란탄), 20 중량%의 Nd(네오디뮴), 5 중량%의 Pr(프라세오디뮴)으로 이루어질 수 있다.Mish metal (Mm) is an element that improves the formability of the sheet at room temperature, and when the content is less than 0.1% by weight, the above effect is hardly obtained, and when the content exceeds 5.0% by weight, the casting temperature is increased due to the high temperature crystallized phase. It is preferable to contain at -5.0 weight%. The mismetal may generally use one kind or a mixture of two or more kinds of elements belonging to atomic numbers 57 (La, lanthanum) to 71 (Lu, lutetium), and cerium rich mismetal (Mm) may be approximately 50% by weight. Ce (cerium), 25 wt% La (lanthanum), 20 wt% Nd (neodymium), 5 wt% Pr (praseodymium).
또한, 본 발명에 따른 마그네슘 합금 판재는, (a) 제1항 내지 제5항 중 어느 한 항에 기재된 마그네슘 합금의 용탕을 650~750℃로 유지하고 스트립 캐스팅 공정을 통해 판재를 주조하는 단계와, (b) 주조된 판재를 200~500℃에서 0.5~48시간 동안 균질화 열처리를 실시하는 단계 및 (c) 균질화 열처리된 판재를 200~500℃로 예열하고, 롤을 25~250℃로 가열한 후 1패스당 50% 이하의 압하율로 열간 압연을 실시하여 최종 압하량이 90% 이하가 되도록 냉간 압연 또는 열간 압연을 실시하는 단계를 통해 제조될 수 있다.In addition, the magnesium alloy sheet according to the present invention comprises the steps of (a) maintaining the molten magnesium alloy of any one of claims 1 to 5 at 650 ~ 750 ℃ and casting the sheet through a strip casting process; (b) performing homogenization heat treatment of the cast plate at 200 to 500 ° C. for 0.5 to 48 hours, and (c) preheating the homogenized heat treatment plate to 200 to 500 ° C., and heating the roll to 25 to 250 ° C. After the hot rolling is carried out at a rolling reduction of 50% or less per pass, it may be manufactured by performing cold rolling or hot rolling so that the final rolling reduction is 90% or less.
상기 용탕의 온도는 650℃ 미만일 경우 주조 시 압하력이 상당히 증가하여 역편석 발생을 증가시키며, 750℃를 초과할 경우 스트립 캐스팅을 할 때 응고가 지연되어 정상적인 판재를 제조할 수 없기 때문에, 650~750℃로 유지하는 것이 바람직하다.When the temperature of the molten metal is less than 650 ° C., the reduction in rolling pressure during casting increases considerably, and the segregation is increased. If the melting temperature is higher than 750 ° C., solidification is delayed when strip casting, and thus, a normal plate cannot be manufactured. It is preferable to keep it at 750 degreeC.
상기 스트립 캐스팅 공정에서 회전하는 롤 속도를 1~10m/min으로 유지하여 용탕이 롤 사이에 빠져나올 때 용탕의 냉각 속도가 102~103K/s가 되도록 한다.In the strip casting process, the rotating roll speed is maintained at 1 to 10 m / min so that the cooling rate of the molten metal is 10 2 to 10 3 K / s when the molten metal escapes between the rolls.
상기 스트립 캐스팅 공정으로 제조된 합금 판재의 중심편석 분율은 2.5%미만을 나타내며, 2.5%를 초과할 경우 균질화 열처리 공정에서 편석부가 재고용되는 과정에서 부피변화 및 리멜팅 현상으로 인해 표면 품질에 악영향을 미치기 때문에, 합금 판재의 중심편석 분율은 2.5%미만으로 유지하는 것이 바람직하다.The center segregation fraction of the alloy sheet produced by the strip casting process is less than 2.5%, and if it exceeds 2.5%, the surface quality is adversely affected by the volume change and remelting in the process of the segregation in the homogenization heat treatment process. Since it is crazy, it is preferable to keep the central segregation fraction of the alloy sheet as less than 2.5%.
상기 공정으로 제조된 합금 판재는 균질화 처리를 수행하는 것이 바람직하며, 이때 균질화 열처리 온도는 300℃ 미만일 경우 열처리에 걸리는 시간이 상당히 길며 500℃를 초과할 경우 부분적으로 용해가 발생하기 때문에 균질화 열처리 온도는 300~500℃가 바람직하고, 균질화 열처리 시간은 30분 미만일 경우 균질화 효과를 달성할 수 없으며, 48시간을 초과할 경우 결정립이 조대화되기 때문에 30분~48시간이 바람직하다.It is preferable to perform the homogenization treatment of the alloy plate produced by the above process, and the homogenization heat treatment temperature is less than 300 ℃, the time required for heat treatment is considerably long, and when it exceeds 500 ℃, the homogenization heat treatment temperature is 300-500 degreeC is preferable, and when a homogenization heat processing time is less than 30 minutes, a homogenization effect cannot be achieved, and when it exceeds 48 hours, 30 minutes-48 hours are preferable because a crystal grain coarsens.
상기 균질화 열처리가 수행된 판재는 박판 제조와 기계적 특성의 향상을 위해 압연을 실시할 수 있으며, 이때 압연 롤의 가열온도는 25℃ 미만일 경우 핫 크래킹(Hot Cracking) 발생이 현저히 증가하고, 250℃를 초과할 경우 압연 시 판재가 롤에 달아붙는 현상이 발생되기 때문에, 롤의 가열온도는 25~250℃가 바람직하다. 또한, 판재의 가열온도는 200℃ 미만일 경우 판재에 에지 크랙 발생이 현저히 증가하고, 500℃ 초과할 경우 부분적으로 판재에서 리멜팅이 발생되기 때문에 판재의 가열온도는 200~500℃인 것이 바람직하다.The plate material subjected to the homogenization heat treatment can be rolled to improve the sheet production and mechanical properties, wherein the hot rolling occurs significantly when the heating temperature of the rolling roll is less than 25 ℃, 250 ℃ When exceeding, since the phenomenon which a board | substrate sticks to a roll at the time of rolling generate | occur | produces, 25-250 degreeC of heating temperature of a roll is preferable. In addition, when the heating temperature of the plate is less than 200 ℃ the generation of edge cracks in the plate significantly increases, and if it exceeds 500 ℃ partially because the remelting occurs in the plate is preferably the heating temperature of the plate is 200 ~ 500 ℃.
1패스당 압하율을 50% 이하가 바람직하고, 최종 압하량 90% 이하로, 냉간 압연 또는 열간 압연을 수행할 수 있다.50% or less of rolling reduction per pass is preferable, and cold rolling or hot rolling can be performed with 90% or less of final rolling reduction.
이하, 본 발명의 실시예들을 기초로 본 발명을 상세하게 설명한다.Hereinafter, the present invention will be described in detail based on the embodiments of the present invention.
마그네슘 합금의 조성Composition of magnesium alloy
본 발명자들은 열역학 전산모사 프로그램인 Pandat 프로그램을 이용하여, 조성별로 합금의 액상선 온도 및 고상선 온도를 예측하는 [식 1] 및 [식 2]를 도출하였으며, 이를 토대로 각 합금별 응고 구간의 크기를 예측하였다.The inventors derived [Formula 1] and [Formula 2] for estimating the liquidus temperature and the solidus temperature of the alloy by composition, using the Pandat program, which is a thermodynamic simulation program, and based on the size of the solidification section of each alloy Was predicted.
[식 1][Equation 1]
액상선 온도(℃) = 650.00 - 5.16Al - 1.33Sn - 3.04Zn + 0.39Mn - 0.12SnAl - 0.06ZnSn - 0.10ZnAl - 0.03MnSn - 0.07MnAl - 0.03MnZn (여기서 Al, Sn, Zn 및 Mn은 이들 원소의 중량%임)Liquidus Temperature (° C) = 650.00-5.16Al-1.33Sn-3.04Zn + 0.39Mn-0.12SnAl-0.06ZnSn-0.10ZnAl-0.03MnSn-0.07MnAl-0.03MnZn (where Al, Sn, Zn and Mn are these elements) Weight percent of
[식 2][Equation 2]
고상선 온도(℃) = 650.00 - 18.51Al - 5.44Sn - 37.89Zn + 0.35Mn - 0.54SnAl - 1.61ZnSn + 1.65ZnAl - 0.2Zn2Al - 0.26MnSn + 1.33MnSn + 1.33MnAl + 1.23MnZn (여기서, Al, Sn, Zn 및 Mn은 이들 원소의 중량%임)Solidus temperature (° C) = 650.00-18.51Al-5.44Sn-37.89Zn + 0.35Mn-0.54SnAl-1.61ZnSn + 1.65ZnAl-0.2Zn 2 Al-0.26MnSn + 1.33MnSn + 1.33MnAl + 1.23MnZn (where Al , Sn, Zn and Mn are the weight percent of these elements)
또한, 상기 식 1 및 식 2로부터 도출된 결과와 실제 합금 간의 상관관계를 확인하기 위하여, 실제 합금을 제조하여 액상선 온도 및 고상선 온도를 측정하였으며, 그 결과를 하기 표 1에 나타내었다.In addition, in order to confirm the correlation between the results derived from Equations 1 and 2 and the actual alloy, the actual alloy was prepared and the liquidus temperature and the solidus temperature were measured, and the results are shown in Table 1 below.
표 1
합금계 (중량%) 액상선 온도(℃) 고상선 온도(℃) 응고 구간(℃)
계산식 Pandat 계산식 Pandat 계산식 Pandat
Mg-6Al 619.0 619.0 538.9 538.0 80.1 81.0
Mg-6Al-0.3Mn 619.0 619.3 541.4 542.0 77.6 77.3
Mg-6Al-1Zn-0.3Mn 615.4 616.0 512.1 507.7 103.3 108.3
Mg-6Al-1Sn-0.3Mn 617.0 617.5 532.7 535.2 84.3 82.3
Mg-6Al-3Sn-0.3Mn 612.8 613.8 515.1 520.5 97.7 93.3
Mg-6Al-3Sn-2Zn-0.3Mn 605.2 606.5 443.5 446.5 161.7 160.0
Mg-1Al-2Sn-1Zn-0.5Mn 638.8 633.1 580.9 587.6 57.9 45.5
Mg-3Al-4Sn-3Zn-0.5Mn 617.0 618.5 444.0 452.6 173.0 165.9
Mg-5Al-5Sn-2Zn-0.3Mn 606.8 608.3 438.2 447.5 168.6 160.8
Table 1
Alloy system (wt%) Liquidus temperature (℃) Solidus temperature (℃) Solidification section (℃)
formula Pandat formula Pandat formula Pandat
Mg-6Al 619.0 619.0 538.9 538.0 80.1 81.0
Mg-6Al-0.3Mn 619.0 619.3 541.4 542.0 77.6 77.3
Mg-6Al-1Zn-0.3Mn 615.4 616.0 512.1 507.7 103.3 108.3
Mg-6Al-1Sn-0.3Mn 617.0 617.5 532.7 535.2 84.3 82.3
Mg-6Al-3Sn-0.3Mn 612.8 613.8 515.1 520.5 97.7 93.3
Mg-6Al-3Sn-2Zn-0.3Mn 605.2 606.5 443.5 446.5 161.7 160.0
Mg-1Al-2Sn-1Zn-0.5Mn 638.8 633.1 580.9 587.6 57.9 45.5
Mg-3Al-4Sn-3Zn-0.5Mn 617.0 618.5 444.0 452.6 173.0 165.9
Mg-5Al-5Sn-2Zn-0.3Mn 606.8 608.3 438.2 447.5 168.6 160.8
상기 표 1에서 확인된 바와 같이, 상기 식 1 및 식 2에서 예측된 응고 구간의 크기는 실제 측정된 합금의 응고 구간과 매우 유사한 결과를 나타냄을 알 수 있다.As confirmed in Table 1, it can be seen that the size of the solidification section predicted in Equations 1 and 2 shows a result very similar to the solidification section of the alloy actually measured.
도 1a ~ 도 1b는, 상기 식 1 및 식 2로부터 도출한 액상선 및 고상선으로부터 Mg-xAl-yZn-0.3Mn 합금계와 Mg-xAl-ySn-0.3Mn 합금계의 조성에 따른 응고 구간을 나타낸 그래프이다.1A to 1B illustrate solidification intervals according to the composition of the Mg-xAl-yZn-0.3Mn alloy system and the Mg-xAl-ySn-0.3Mn alloy system from the liquidus and solidus lines derived from Equations 1 and 2; The graph shown.
도 1에 보이는 바와 같이, Zn 대신 Sn를 첨가하면 응고 구간의 크기가 감소하는 것을 볼 수 있으며, 이는 스트립 캐스팅 시 중심편석 내지 역편석의 감소로 이어질 수 있다.As shown in Figure 1, it can be seen that the addition of Sn instead of Zn decreases the size of the solidification section, which may lead to a reduction in central segregation to reverse segregation during strip casting.
표 2
순번 명칭 조성 (중량%) 비고
Al Sn Mn Ca RE Zn Mg
No.1 A6 6.0 - 0.3 - - - Bal. 실시예
No.2 AZ60 6.0 - 0.3 - - 0.3 Bal. 비교예
No.3 AZ61 6.0 - 0.3 - - 1 Bal. 비교예
No.4 AM61 6.0 - 1.0 - - - Bal. 실시예
No.5 AMX610 6.0 - 1.0 0.3 - - Bal. 실시예
No.6 AMX611 6.0 - 1.0 1.0 - - Bal. 실시예
No.7 AME610 6.0 - 1.0 - 0.3 - Bal. 실시예
No.8 AME611 6.0 - 1.0 - 1.0 - Bal. 실시예
No.9 AT63 6.0 3.0 0.3 - - - Bal. 실시예
No.10 ATX630 6.0 3.0 0.3 0.3 - - Bal. 실시예
No.11 ATX631 6.0 3.0 0.3 1.0 - - Bal. 실시예
No.12 ATE630 6.0 3.0 0.3 - 0.3 - Bal. 실시예
No.13 ATE631 6.0 3.0 0.3 - 1.0 - Bal. 실시예
No.14 AT67 6.0 7.0 0.3 - - - Bal. 비교예
TABLE 2
turn designation Composition (wt%) Remarks
Al Sn Mn Ca RE Zn Mg
No.1 A6 6.0 - 0.3 - - - Bal. Example
No.2 AZ60 6.0 - 0.3 - - 0.3 Bal. Comparative example
No.3 AZ61 6.0 - 0.3 - - One Bal. Comparative example
No.4 AM61 6.0 - 1.0 - - - Bal. Example
No.5 AMX610 6.0 - 1.0 0.3 - - Bal. Example
No.6 AMX611 6.0 - 1.0 1.0 - - Bal. Example
No.7 AME610 6.0 - 1.0 - 0.3 - Bal. Example
No.8 AME611 6.0 - 1.0 - 1.0 - Bal. Example
No.9 AT63 6.0 3.0 0.3 - - - Bal. Example
No.10 ATX630 6.0 3.0 0.3 0.3 - - Bal. Example
No.11 ATX631 6.0 3.0 0.3 1.0 - - Bal. Example
No.12 ATE630 6.0 3.0 0.3 - 0.3 - Bal. Example
No.13 ATE631 6.0 3.0 0.3 - 1.0 - Bal. Example
No.14 AT67 6.0 7.0 0.3 - - - Bal. Comparative example
상기 표 2의 합금 조성은, 상기한 응고 구간의 크기와, 첨가되었을 때 마그네슘 합금의 기계적 특성에 미치는 영향을 고려하여 선정된 것이며, 상기 표 2에서 No.2, No.3 및 No.14 합금은 본 발명의 실시예에 따른 합금과의 비교를 위한 것이다.The alloy composition of Table 2 is selected in consideration of the size of the solidification section and the effect on the mechanical properties of the magnesium alloy when added, and in Table 2, No. 2, No. 3 and No. 14 alloys. Is for comparison with an alloy according to an embodiment of the invention.
마그네슘 합금 판재의 제조Manufacture of Magnesium Alloy Plate
마그네슘 합금 판재는 도 2에 개략적으로 도시된 스트립 캐스팅 장치를 이용하여 제조하였다. 구체적으로 상기 스트립 캐스팅 장치는 Cu-Be 합금으로 이루어진 쌍롤(10)과, 용탕을 수용하는 도가니(20)와, 상기 도가니(20)로부터 용탕을 상기 쌍롤(10)로 주입하는 노즐(30)과, 상기 도가니(20) 내에 배치되어 용탕을 노즐로 보내도록 하는 펜들럼(40)과 상기 도가니를 수용하고 일정 이상의 온도로 유지하게 하는 핫 챔버(50)를 포함한다. 이때 상기 롤의 직경은 140mm 이다.Magnesium alloy plate was produced using a strip casting apparatus schematically shown in FIG. Specifically, the strip casting apparatus includes a twin roll 10 made of a Cu-Be alloy, a crucible 20 accommodating molten metal, a nozzle 30 for injecting molten metal from the crucible 20 to the pair roll 10, and And a pendulum 40 disposed in the crucible 20 to direct the molten metal to the nozzle and a hot chamber 50 to receive the crucible and maintain the temperature at a predetermined temperature or higher. At this time, the diameter of the roll is 140mm.
상기 표 1과 같이 준비된 합금을 용탕온도 700~720℃, 롤속도 3~4mpm, 롤갭 2mm 조건을 적용하여 마그네슘 합금 판재를 제조하였다.The alloy prepared as shown in Table 1 was prepared by applying a melt temperature of 700 ~ 720 ℃, roll speed 3 ~ 4mpm, roll gap 2mm conditions.
미세조직 분석Microstructure Analysis
이와 같이 제조된 마그네슘 합금 판재에 나타난 편석을 관찰하기 위하여, 스트립 캐스팅 공정으로 제조한 판재에서 횡단 방향으로 시편을 채취하였으며, 각 시편은 4000번까지의 사포를 사용하여 기계적 연마를 행한 후 0.05mm 알루미나 분말을 사용하여 최종 미세 연마를 실시하였다. 이와 같이 연마된 시편을 0.5% 나이탈(Nital) 용액으로 에칭한 후 광학현미경을 이용하여 미세조직을 관찰하였다.In order to observe the segregation in the magnesium alloy sheet thus prepared, specimens were taken in the transverse direction from the sheet produced by the strip casting process, and each specimen was subjected to mechanical polishing using sandpaper up to 4000 times, followed by 0.05 mm alumina. The final fine polishing was performed using the powder. The polished specimens were etched with 0.5% nital solution and then microstructures were observed using an optical microscope.
도 3a는 실시예 No.1 스트립 캐스트 판재의 주조방향에서 관찰한 미세조직 사진이다. 도 3에서 확인되는 바와 같이, Zn이 첨가된 AZ60와 AZ61합금의 최종 응고 부분인 판재의 중심부에서 편석이 생성된 것을 볼 수 있으며, 판재 중심편석 분율이 각각 3.30% 및 2.66%인 것을 확인하였다. 이는 일반적으로 분배계수가 1보다 작은 Al과 Zn의 용질 원자들이 판재의 표면으로부터 재분배하기 때문이다. 저융점합금 원소인 Zn가 첨가된 합금계는 적은 양을 첨가하여도 고상선 온도가 낮아져 상대적으로 많은 양의 중심 편석을 생성하며 스트립 캐스팅 공정에는 적합하지 않은 합금계임을 알 수 있다.3A is a microstructure photograph of Example No. 1 strip cast sheet observed in the casting direction. As can be seen in Figure 3, it can be seen that segregation was generated in the center of the plate, which is the final solidified portion of the Zn-added AZ60 and AZ61 alloy, the plate segregation was found to be 3.30% and 2.66%, respectively. This is because solute atoms of Al and Zn having a partition coefficient of less than 1 are redistributed from the surface of the sheet. It can be seen that an alloy system containing Zn, which is a low melting point alloy element, has a low solidus temperature even when a small amount is added, thereby generating a relatively large amount of central segregation and is not suitable for the strip casting process.
하기 표 3은 본 발명의 실시예 및 비교예에 따른 마그네슘 합금으로 스트립 캐스팅된 판재의 중심편석 분율을 나타내었으며, 이미지 분석 프로그램인 ImageJ를 이용하여 중심편석의 분율을 계산하였으며 중심편석의 면적과 판재의 전체면적을 고려하였다.Table 3 shows the central segregation fraction of the plate strip cast with magnesium alloy according to the Examples and Comparative Examples of the present invention, the fraction of the central segregation was calculated using ImageJ, an image analysis program, the area and the area of the central segregation The total area of is taken into account.
표 3
합금번호 조성 주조방향 중심편석 분율(%) 비고
1 A6 2.29 실시예
2 AZ60 3.30 비교예
3 AZ61 2.66 비교예
4 AM61 1.24 실시예
5 AMX610 1.96 실시예
6 AMX611 2.12 실시예
7 AME610 1.79 실시예
8 AME611 1.17 실시예
9 AT63 1.55 실시예
10 ATX630 1.90 실시예
11 ATX631 2.34 실시예
12 ATE630 2.36 실시예
13 ATE631 1.21 실시예
14 AT67 6.20 비교예
TABLE 3
Alloy number Furtherance Casting direction center segregation fraction (%) Remarks
One A6 2.29 Example
2 AZ60 3.30 Comparative example
3 AZ61 2.66 Comparative example
4 AM61 1.24 Example
5 AMX610 1.96 Example
6 AMX611 2.12 Example
7 AME610 1.79 Example
8 AME611 1.17 Example
9 AT63 1.55 Example
10 ATX630 1.90 Example
11 ATX631 2.34 Example
12 ATE630 2.36 Example
13 ATE631 1.21 Example
14 AT67 6.20 Comparative example
표 3에서 확인되는 바와 같이, AT67 합금을 제외한 다른 실시 예에서는 중심 편석 분율이 Mg-6Al-xZn 합금보다 적게 생성하는 것을 볼 수 있었다. AT67 합금의 중심편석 분율은 6.20%으로 Mg-6Al-xZn 합금보다 많이 생성되었으며, Al 합금원소가 6.0중량이 포함된 마그네슘 합금의 Sn 고용한이 대략 6.0중량이기 때문에 Sn 합금원소가 7.0중량이 포함된 AT67 합금의 경우 상대적으로 많은 양의 중심편석이 생성되는 것을 볼 수 있다.As can be seen from Table 3, in other examples except for the AT67 alloy, it was found that the central segregation fraction is generated less than the Mg-6Al-xZn alloy. The central segregation fraction of the AT67 alloy was 6.20%, which was higher than that of the Mg-6Al-xZn alloy, and the Sn alloying element included 7.0 weights because the Sn solid solution of the magnesium alloy containing 6.0 weights of Al alloys was about 6.0 weights. In the case of the AT67 alloy, it can be seen that a relatively large amount of central segregation is generated.
주조재 균질화 열처리 및 압연재 제조Casting material homogenization heat treatment and rolling material manufacture
스트립 캐스팅된 마그네슘 판재의 내외부에는 편석 및 결함이 혼재되어 있으므로 압연시 균열이 발생하기 쉬우며, 이를 제거하기 위해 균질화 열처리를 실시해야한다. 균질화 열처리는 400℃에서 12시간 실시하였으며, 균질화 열처리된 판재를 350℃에 예열한 후 200℃로 가열된 압연 롤에서 1패스당 압하율 15% 조건에서 열간압연을 실시하였다.Since segregation and defects are mixed inside and outside of the strip-cast magnesium sheet, cracking is likely to occur during rolling, and homogenization heat treatment must be performed to remove it. The homogenization heat treatment was carried out at 400 ° C. for 12 hours. The homogenized heat-treated plate was preheated to 350 ° C. and then hot rolled at a rolling rate of 15% in a rolling roll heated to 200 ° C.
상온 인장 특성 평가Evaluation of room temperature tensile properties
이상과 같이 스트립 캐스트, 균질화 열처리 및 열간 압연을 실시한 마그네슘판재의 기계적 특성을 평가하기 위해 상온에서 2×10-4/s의 공칭변형률속도로 인장시험을 실시하였으며, 그 결과는 하기 표 4와 같다.In order to evaluate the mechanical properties of the magnesium sheet subjected to strip cast, homogenization heat treatment and hot rolling as described above, a tensile test was performed at a nominal strain rate of 2 × 10 −4 / s at room temperature, and the results are shown in Table 4 below. .
표 4
합금번호 합금 조성 항복강도 (MPa) 인장강도 (MPa) 연신율 (%)
1 A6 178.7 296.1 20.0
3 AZ61 189.7 301.5 17.1
4 AM61 186.3 294.9 19.6
5 AMX610 193.7 302.8 20.1
6 AMX611 203.4 295.7 12.9
7 AME610 185.0 293.7 22.1
8 AME611 188.9 286.1 9.7
9 AT63 180.7 305.8 21.7
10 ATX630 190.0 318.2 20.8
11 ATX631 197.8 309.9 13.1
12 ATE630 180.3 301.3 16.1
13 ATE631 187.3 303.4 18.3
Table 4
Alloy number Alloy composition Yield strength (MPa) Tensile Strength (MPa) Elongation (%)
One A6 178.7 296.1 20.0
3 AZ61 189.7 301.5 17.1
4 AM61 186.3 294.9 19.6
5 AMX610 193.7 302.8 20.1
6 AMX611 203.4 295.7 12.9
7 AME610 185.0 293.7 22.1
8 AME611 188.9 286.1 9.7
9 AT63 180.7 305.8 21.7
10 ATX630 190.0 318.2 20.8
11 ATX631 197.8 309.9 13.1
12 ATE630 180.3 301.3 16.1
13 ATE631 187.3 303.4 18.3
상기 표 4에 나타난 바와 같이, 상용합금인 AZ61합금의 인장강도가 301.5MPa인데, 본 발명의 실시예에 따른 합금들은 AZ61합금에 비해 앞에서 살펴본 바와 같이 중심편석이 낮으면서도 285MPa 이상의 인장강도의 구현이 가능하며, 특히 AMX610 및 ATX630합금의 경우, 그 인장강도가 각각 302.5MPa, 318.2MPa으로 AZ61합금보다 더 우수하게 구현됨을 알 수 있었다.As shown in Table 4, the tensile strength of the commercial alloy AZ61 alloy is 301.5MPa, alloys according to the embodiment of the present invention as compared to the AZ61 alloy as described above, while the lower the center segregation as described above, the implementation of tensile strength of 285MPa or more In particular, in the case of AMX610 and ATX630 alloys, the tensile strengths of 302.5 MPa and 318.2 MPa were found to be better than those of the AZ61 alloy.

Claims (10)

  1. Al:3.0초과~10.0중량%를 함유하고, 나머지는 마그네슘과 불가피한 불순물로 이루어진 마그네슘 합금을 스트립 캐스팅을 포함하는 공정으로 제조한 것으로, 판재 편석 분율이 2.5%이하인 마그네슘 합금 판재.A magnesium alloy sheet containing Al: more than 3.0 to 10.0% by weight, the remainder being manufactured by a process including strip casting of a magnesium alloy composed of magnesium and unavoidable impurities, and having a sheet segregation fraction of 2.5% or less.
  2. Al:3.0초과~10.0중량%와 Sn:0.1~6.0중량%를 함유하고, 나머지는 마그네슘과 불가피한 불순물로 이루어진 마그네슘 합금을 스트립 캐스팅을 포함하는 공정으로 제조한 것으로, 판재 편석 분율이 2.5%이하인 마그네슘 합금 판재.Magnesium containing more than 3.0% to 10.0% by weight of Al and 0.1% to 6.0% by weight of Sn, the remainder being manufactured by a process including strip casting of magnesium and inevitable impurities, and having a plate segregation ratio of 2.5% or less Alloy plate.
  3. Al:3.0초과~10.0중량%와 Mn:0.1~3.0중량%를 함유하고, 나머지는 마그네슘과 불가피한 불순물로 이루어진 마그네슘 합금을 스트립 캐스팅을 포함하는 공정으로 제조한 것으로, 판재 편석 분율이 2.5%이하인 마그네슘 합금 판재.Magnesium alloy containing Al: more than 3.0% to 10.0% by weight and Mn: 0.1% to 3.0% by weight, and the rest is made of a magnesium alloy composed of magnesium and unavoidable impurities by a process including strip casting. Alloy plate.
  4. Al:3.0초과~10.0중량%, Sn:0.1~6.0중량%, 및 Ca:0.1~5.0중량% 또는 미쉬메탈:0.1~5.0중량% 중 어느 하나를 함유하고, 나머지는 마그네슘과 불가피한 불순물로 이루어진 마그네슘 합금을 스트립 캐스팅을 포함하는 공정으로 제조한 것으로, 판재 편석 분율이 2.5%이하인 마그네슘 합금 판재.Magnesium containing more than 3.0% to 10.0% of Al, 0.1% to 6.0% by weight of Sn, and 0.1% to 5.0% by weight of Ca, or 0.1% to 5.0% by weight of misch metal, the remainder being magnesium composed of magnesium and unavoidable impurities Magnesium alloy sheet produced by the process including the strip casting, the plate segregation fraction is 2.5% or less.
  5. Al:3.0초과~10.0중량%, Mn:0.1~3.0중량%, 및 Ca:0.1~5.0중량% 또는 미쉬메탈:0.1~5.0중량% 중 어느 하나를 함유하며, 나머지는 마그네슘과 불가피한 불순물로 이루어진 마그네슘 합금을 스트립 캐스팅을 포함하는 공정으로 제조한 것으로, 판재 편석 분율이 2.5%이하인 마그네슘 합금 판재.Al: more than 3.0% to 10.0% by weight, Mn: 0.1% to 3.0% by weight, and Ca: 0.1% to 5.0% by weight or misch metal: 0.1% to 5.0% by weight, the rest being magnesium composed of magnesium and unavoidable impurities Magnesium alloy sheet produced by the process including the strip casting, the plate segregation fraction is 2.5% or less.
  6. 제1항 내지 제5항 중 어느 한 항에 있어서,The method according to any one of claims 1 to 5,
    상기 편석분율은 2.0% 이하인 마그네슘 합금 판재.The segregation fraction is less than 2.0% magnesium alloy plate.
  7. 제4항 또는 제5항에 있어서,The method according to claim 4 or 5,
    상기 미쉬메탈은 원자번호 57(La, 란탄) 내지 71(Lu, 루테튬)에 속하는 원소의 1종 또는 2종 이상의 혼합물을 포함하는 마그네슘 합금 판재.Mash metal is a magnesium alloy sheet containing one or a mixture of two or more of the elements belonging to the atomic number 57 (La, lanthanum) to 71 (Lu, lutetium).
  8. 제4항 또는 제5항에 있어서,The method according to claim 4 or 5,
    상기 미쉬메탈은 세륨리치 미시메탈인 마그네슘 합금 판재.Mish metal is a magnesium alloy sheet material of cerium rich mismetal.
  9. 제3항 또는 제5항에 있어서, The method according to claim 3 or 5,
    상기 Mn의 함량은 0.1~0.3중량%인 마그네슘 합금 판재.Mn content is 0.1 to 0.3% by weight magnesium alloy sheet material.
  10. (a) 제1항 내지 제5항 중 어느 한 항에 기재된 마그네슘 합금의 용탕을 650~750℃로 유지하고 스트립 캐스팅 공정을 통해 판재를 주조하는 단계;(A) maintaining the molten metal of the magnesium alloy according to any one of claims 1 to 5 at 650 ~ 750 ℃ and casting a plate through a strip casting process;
    (b) 주조된 판재를 200~500℃에서 0.5~48시간 동안 균질화 열처리를 실시하는 단계; 및 (b) performing homogenization heat treatment of the cast plate at 200 to 500 ° C. for 0.5 to 48 hours; And
    (c) 균질화 열처리된 판재를 200~500℃로 예열하고, 롤을 25~250℃로 가열한 후 1패스당 50% 이하의 압하율로 열간 압연을 실시하여 최종 압하량이 90% 이하가 되도록 냉간 압연 또는 열간 압연을 실시하는 단계;를 포함하는 마그네슘 합금 판재의 제조방법.(c) Preheat the homogenized heat-treated plate to 200 ~ 500 ℃, heat the roll to 25 ~ 250 ℃ and perform hot rolling at 50% or less rolling rate per pass, so that the final rolling amount is 90% or less. Method of producing a magnesium alloy sheet comprising a; performing rolling or hot rolling.
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Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109084008A (en) * 2018-08-27 2018-12-25 重庆元和利泰镁合金制造有限公司 Magnesium alloy gear box casing and preparation method thereof
CN113981286A (en) * 2021-11-01 2022-01-28 吉林大学 Corrosion-resistant high-strength plastic magnesium alloy and preparation method thereof
CN114908278A (en) * 2021-02-08 2022-08-16 通用汽车环球科技运作有限责任公司 Magnesium alloy and forged component
CN115305395A (en) * 2022-08-15 2022-11-08 吉林大学 High-strength-plasticity Mg-Al-Sn-Ca-RE alloy and preparation method thereof
WO2023004851A1 (en) * 2021-07-27 2023-02-02 广东铭利达科技有限公司 High-strength corrosion-resistant magnesium alloy composite material and preparation method therefor

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2018117695A1 (en) 2016-12-22 2018-06-28 주식회사 포스코 Magnesium alloy sheet and method for manufacturing same

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20070096477A (en) * 2006-03-24 2007-10-02 (주)이노캐스트 Magnesium alloy having heat resisting property
JP2011157626A (en) * 2005-03-28 2011-08-18 Sumitomo Electric Ind Ltd Magnesium alloy sheet
KR20140002726A (en) * 2011-02-14 2014-01-08 스미토모덴키고교가부시키가이샤 Rolled magnesium alloy material, magnesium alloy member, and method for producing rolled magnesium alloy material
KR20140004710A (en) * 2011-02-24 2014-01-13 스미토모덴키고교가부시키가이샤 Magnesium alloy material and method for producing the same

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2011157626A (en) * 2005-03-28 2011-08-18 Sumitomo Electric Ind Ltd Magnesium alloy sheet
KR20070096477A (en) * 2006-03-24 2007-10-02 (주)이노캐스트 Magnesium alloy having heat resisting property
KR20140002726A (en) * 2011-02-14 2014-01-08 스미토모덴키고교가부시키가이샤 Rolled magnesium alloy material, magnesium alloy member, and method for producing rolled magnesium alloy material
KR20140004710A (en) * 2011-02-24 2014-01-13 스미토모덴키고교가부시키가이샤 Magnesium alloy material and method for producing the same

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109084008A (en) * 2018-08-27 2018-12-25 重庆元和利泰镁合金制造有限公司 Magnesium alloy gear box casing and preparation method thereof
CN114908278A (en) * 2021-02-08 2022-08-16 通用汽车环球科技运作有限责任公司 Magnesium alloy and forged component
US11987864B2 (en) 2021-02-08 2024-05-21 GM Global Technology Operations LLC Magnesium alloy and forged component
WO2023004851A1 (en) * 2021-07-27 2023-02-02 广东铭利达科技有限公司 High-strength corrosion-resistant magnesium alloy composite material and preparation method therefor
CN113981286A (en) * 2021-11-01 2022-01-28 吉林大学 Corrosion-resistant high-strength plastic magnesium alloy and preparation method thereof
CN113981286B (en) * 2021-11-01 2022-06-21 吉林大学 Corrosion-resistant high-strength plastic magnesium alloy and preparation method thereof
CN115305395A (en) * 2022-08-15 2022-11-08 吉林大学 High-strength-plasticity Mg-Al-Sn-Ca-RE alloy and preparation method thereof

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