WO2017111550A1 - Matériau de tôle d'alliage de magnésium et procédé de fabrication associé - Google Patents

Matériau de tôle d'alliage de magnésium et procédé de fabrication associé Download PDF

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Publication number
WO2017111550A1
WO2017111550A1 PCT/KR2016/015228 KR2016015228W WO2017111550A1 WO 2017111550 A1 WO2017111550 A1 WO 2017111550A1 KR 2016015228 W KR2016015228 W KR 2016015228W WO 2017111550 A1 WO2017111550 A1 WO 2017111550A1
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Prior art keywords
magnesium alloy
alloy sheet
producing
rolled
manufacturing
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PCT/KR2016/015228
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English (en)
Korean (ko)
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WO2017111550A8 (fr
Inventor
박준호
rnjsdhejr
이현범
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.)
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Priority claimed from KR1020150185017A external-priority patent/KR20170075407A/ko
Priority claimed from KR1020150186295A external-priority patent/KR101751521B1/ko
Application filed by 주식회사 포스코 filed Critical 주식회사 포스코
Priority to CN201680075821.9A priority Critical patent/CN108472699B/zh
Priority to JP2018532629A priority patent/JP6758383B2/ja
Priority to EP16879417.0A priority patent/EP3395458B1/fr
Priority to US16/065,562 priority patent/US20190093200A1/en
Publication of WO2017111550A1 publication Critical patent/WO2017111550A1/fr
Publication of WO2017111550A8 publication Critical patent/WO2017111550A8/fr

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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
    • 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

  • Magnesium alloy plate and a manufacturing method thereof.
  • magnesium is the lightest metal with a density of 1.74 g / ciii ', compared to other structural materials such as aluminum and steel, and has various advantages such as vibration absorbing ability and electromagnetic shielding ability. Is being actively researched.
  • Such magnesium-containing alloys are mainly applied to automotive fields as well as electronic devices, but there is a fundamental problem in corrosion resistance, flame retardancy, and moldability, and thus there is a limit to further extending the application range. '
  • magnesium is a HCP structure (Hexagonal Closed Packed Structure), there is not enough slip system at room temperature, there are many difficulties in the machining process. In other words, the processing of magnesium requires a lot of heat, which leads to an increase in process costs.
  • the AZ-based alloy includes aluminum (A1) and zinc (Zn), and is a commercially available magnesium alloy because it is inexpensive while securing appropriate strength and ductility to some extent.
  • the above-mentioned physical properties mean that it is a moderate degree in magnesium alloy to the last, and it is a low strength compared with aluminum (A1) which is a competitive material. Therefore, it is necessary to improve the physical properties such as low formability and strength of the AZ-based magnesium alloy, but there is still a lack of research on this.
  • An object of the present invention is to provide a magnet alloy sheet alloy sheet having improved strength and formability, and a method of manufacturing the same.
  • the magnesium alloy sheet alloy sheet according to an embodiment of the present invention is A1: 2.7 to 5% by weight, Zn: 0.75 to 1% by weight, Ca: 0.1 to 1% by weight and Mn: 1% by weight or less (excluding 0% by weight) And the rest consists of Mg and unavoidable impurities.
  • Ca 0.3 to 0.8% by weight can be contained.
  • the magnesium alloy sheet metal sheet may include Al-Ca secondary phase particles including A1: 20 to 25 weight percent Ca: 5 to 10 weight percent, Mn: 0.1 to 0.5 weight percent, Zn: 0.5 to 1 weight percent, and the remaining Mg. Can be.
  • the average particle diameter of the Al-Ca secondary phase particles may be 0.01 to 4; ⁇ .
  • Al-Ca secondary phase particles may include 5 to 15 per 100 ⁇ 2 of the magnesium alloy sheet alloy sheet material.
  • the magnesium alloy alloy sheet material includes grains, and the average grain size of the grains may be 5 to 30 days.
  • the magnesium alloy sheet material may have a thickness of 0.4 to 3 mm.
  • Method for producing a magnesium alloy sheet according to an embodiment of the present invention is A1: 2.7 to 5% by weight, Zn: 0.75 to 1% by weight Ca: 0.1 to 1% by weight and Mn: 1% by weight or less (excluding 0% by weight) Casting a molten metal, the remainder comprising Mg and unavoidable impurities to prepare a casting material; Homogenizing heat treatment of the casting material; And warm rolling the homogenized cast material.
  • the reduction force may be 0.2ton / nini 2 or more. More specifically, it may be at least on It / mm 2 . Even more specifically, it may be 1 to 1.5 ton / mm 2 or more.
  • the cast material may be subjected to homogenization heat treatment for 1 to 28 hours at a temperature of 350 to 500 ° C. More specifically, the homogenization heat treatment can be performed for 18 to 28 hours.
  • It can be hot rolled at a temperature of 150 to 350 ° C. More specifically, it may be silver rolled at a temperature of 200 to 300 ° C.
  • Warm rolling may be performed a plurality of times, and may be rolled in silver at a reduction ratio of 10 to 30% per time.
  • Intermediate annealing in the middle of the plurality of warm rolling may further comprise one or more times.
  • the intermediate annealing may be carried out at a temperature of 300 to 500 ° C. More specifically, it can be carried out at a temperature of 450 to 500 ° C. More specifically, it may be carried out for 1 to 10 hours.
  • Post-heat treatment may be carried out at 300 to 500 ° C for 1 to 10 hours.
  • Magnesium alloy sheet and a manufacturing method of an embodiment of the present invention A1: 2.7wt% or more and 5wt% or less, Zn: 0.75% or more and lwt% or less, Ca: 0.1wt% or more 1 ⁇ 4 «Aha, Mn : Preparing a master alloy containing more than 0 wt% and less than 1% and the residual unavoidable impurities and magnesium; Casting the master alloy to produce a casting material; Homogenizing heat treatment of the casting material; Manufacturing a rolled material by rolling the homogenized heat-treated casting material; Post-heat treating the rolled material; And performing a skin pass on the post-heat-treated rolled material to produce a magnesium alloy sheet material. It may include.
  • Manufacturing a magnesium alloy sheet by performing a skin pass on the post-heat-treated rolled material In, the skin pass may be performed once, the skin pass may be carried out in a temperature range of 250 ° C to 350 ° C.
  • the prepared magnesium alloy sheet material can be rolled at a 2 to 15% reduction ratio with respect to the thickness of the rolled material. More Specifically, the prepared magnesium alloy sheet material for the thickness of the rolled material
  • the first heat treatment step in the temperature range of 300 ° C to 400 ° C; And a second heat treatment step in the silver road section at 400 ° C to 500 ° C .; It may include.
  • Primary heat treatment step in the temperature range of 300 ° C to 400 ° C; May be performed for 5 hours to 20 hours.
  • the cast material may be rolled to a thickness range of 0.4 to 3 kPa.
  • the cast material may be rolled 1 to 15 times.
  • Manufacturing a rolled material by rolling the homogenized heat-treated casting material It can be carried out at 150 ° C to 350 ° C.
  • the ' rolled material may be annealed for 1 hour to 15 hours in the temperature range of 300 ° C to 550 ° C.
  • the limit height (LDH) of the magnesium alloy plate may be greater than or equal to 7 ⁇ . More specifically, the limit dome height (LDH) of the magnesium alloy plate may be greater than or equal to 8 ⁇ .
  • Maximum aggregate strength may be 1 to 4 based on the magnesium alloy plate (0001) surface.
  • the yield strength of the magnesium alloy sheet may be 170 to 300MPa.
  • the center segregation easily generated in the existing magnesium alloy sheet is removed, it is possible to provide a magnesium alloy sheet with improved formability.
  • the aggregate structure in the magnesium alloy sheet is uniformly dispersed, it is possible to provide a magnesium alloy sheet with improved moldability.
  • the magnesium alloy sheet in the magnesium alloy sheet
  • Al-Ca secondary particles may be formed to provide a magnesium alloy sheet having improved strength.
  • Magnesium alloy sheet manufacturing method it is possible to provide a magnesium alloy sheet excellent in strength and formability by controlling the manufacturing process of commercialized magnesium alloy. This can be applied to future automotive parts or IT mobile devices.
  • FIG. 1 is a schematic flowchart of a method of manufacturing a magnesium alloy sheet according to an embodiment of the present invention.
  • FIG. 2 is a scanning electron microscope (SEM) photograph of the magnet alloy plate prepared in Example 1.
  • SEM scanning electron microscope
  • Example 4 is a secondary of the magnesium alloy sheet prepared in Example 1
  • Example 5 is a photograph of the result of measuring the limit dynamic height of the magnesium alloy sheet manufactured in Example 1;
  • Example 6 is a result of analyzing the crystal orientation by the XRD analyzer of the magnesium alloy sheet prepared in Example 1.
  • Example 8 is a photograph of EBSD (Electron Backseat ter Di-fract ion) of the magnesium alloy sheet prepared in Example 1.
  • Figure 10 shows the aggregate strength of the (0001) plane of the examples and comparative examples of the present application.
  • the terms first, second and third are used to describe various parts, components, regions, layers and / or sections, but are not limited to these. These terms refer to any part, component, region, filler, or section as another part, component, region. Only used to distinguish it from layers or sections. Accordingly, the first portion, component, region, layer or section described below may be referred to as the second portion, component, region, layer or section without departing from the scope of the invention.
  • % means weight% ( ⁇ %).
  • Magnesium alloy sheet according to an embodiment of the present invention is A1: 2.7 to 5% by weight, Zn: 0.75 to 1% by weight Ca: 0.01 to 1% by weight, Mn: 1% by weight or less (excluding 0% by weight) And the rest consists of Mg and unavoidable impurities.
  • aluminum (A l) is magnesium . It improves the mechanical properties of the alloy sheet and improves the castability of the molten metal. If A 1 is added too much, the castability may be rapidly deteriorated. If A 1 is added too little, the mechanical properties of the magnesium alloy sheet may be deteriorated. Therefore, the content range of A 1 can be adjusted to the above-described range.
  • Zinc (Zn) improves the mechanical properties of magnesium alloy plates. If too much Zn is added, a large amount of surface defects and central segregation may be generated, which may cause a problem of rapid deterioration of castability, and if too little Zn is added, a problem of deterioration of mechanical properties of the magnesium alloy sheet may occur. . Therefore, the content range of Zn can be adjusted within the above range.
  • Chest (Ca) imparts flame retardancy to the magnesium alloy sheet.
  • Ca Chest
  • problems may occur such that the flowability of the molten metal is reduced, castability is deteriorated, and central segregation of Al-Ca based intermetallic material is generated, which deteriorates the formability of the magnesium alloy sheet. If too little is added, a problem may arise that the flame retardancy is not sufficiently given. Therefore, the content range of Ca can be adjusted within the above range. More specifically Ca is from 0.3 to 0. 8 weight% may be included.
  • Manganese (Mn) improves the mechanical properties of the magnesium alloy sheet. If too much Mn is added, a problem may arise that the heat dissipation is deteriorated and uniform distribution control may be difficult. Therefore, the content range of Mn can be adjusted within the above range.
  • Magnesium alloy sheet according to an embodiment of the present invention is A 1: 20 to 25% by weight, Ca: 5 to 10% by weight, Mn: 0.1 to 0.5% by weight, Zn: 0.5 to 1% by weight And it may include Al-Ca secondary phase particles including the remaining Mg.
  • the magnesium alloy sheet according to an embodiment of the present invention includes Al—Ca secondary particles, thereby improving formability.
  • the average particle diameter of the Al-Ca secondary phase particles may be 0.01 to 4 mm 3. The moldability can be further improved in the above-described range.
  • the Al-Ca secondary phase particles of the magnesium alloy sheet 5 to 15 may be included per 100 2 area.
  • the formability of the magnesium alloy sheet can be further improved.
  • the composition ranges of Al, Zn, Mn, and Ca, silver and time conditions during homogenization heat treatment, silver rolling, temperature and rolling rate need to be precisely controlled.
  • the magnesium alloy sheet includes grains, and the average grain size of the grains may be 5 to 30.
  • the moldability can be further improved in the above-described range.
  • it is necessary to precisely control the composition range of Al, Zn, Mn and Ca, temperature and time conditions during homogenization heat treatment, temperature and rolling rate during warm rolling.
  • the limiting height (l imiting dome height) of the magnesium alloy sheet according to an embodiment of the present invention may be 7 k ⁇ or more. More specifically, it may be 8 uiui or more, and more specifically 8 to 10 ran.
  • the limit dome height is used as an index for evaluating the formability (particularly compressibility) of the material, and as the limit dome height increases, the formability of the material is improved.
  • the limited range is due to the increased grain orientation distribution in the magnesium alloy sheet, which is a significantly higher limit dome height than the generally known magnesium alloy sheet.
  • the thickness of the magnesium alloy sheet according to an embodiment of the present invention may be 0.4 to 3 kPa.
  • FIG. 1 schematically shows a flowchart of a method of manufacturing a magnesium alloy sheet according to an embodiment of the present invention.
  • the flowchart of the manufacturing method of the magnesium alloy plate material of FIG. 1 is for illustration only, and this invention is not limited to this. Therefore, the manufacturing method of a magnesium alloy plate material can be variously modified.
  • Method for producing a magnesium alloy sheet according to an embodiment of the present invention is A1-: 2.7 to 5% by weight, Zn: 0.75 to 1% by weight, Ca: 0.01 to 1% by weight and Mn: 1% by weight or less (0 Casting a molten metal containing an increase in%) and the remainder of Mg and unavoidable impurities Step (Sl ' O), the step of homogenizing heat treatment of the cast material (S20) and the step (S30) of silver-rolling the homogenized cast material.
  • the method of manufacturing a magnesium alloy sheet may further include other steps.
  • step S10 A1: 2.7 to 5% by weight, Zn: 0.75 to 1% by weight, Ca: 0.1 to 1% by weight and Mn: 1% by weight or less (excluding 0% by weight), and the rest Cast a molten metal consisting of Mg and unavoidable impurities to produce a casting material.
  • the method of manufacturing the casting material die casting, strip casting, billet casting, centrifugal casting, tilt casting, sand casting, direct chill casting (Direct chill casting) or a combination thereof may be used. More specifically, the strip casting method can be used. It is not limited to words.
  • 0.2 ton / mm 2 or more More specifically, it may be at least on It / mm 2 . More specifically, it may be 1 to 1.5 ton / mm 2 or more.
  • Casting can be made by casting. At this time, the cast material is uneven and at the same time receives a reduction force, by adjusting the reduction force in the above range, it is possible to improve the formability of the magnesium alloy sheet.
  • the cast material is homogenized and heat treated.
  • the heat treatment conditions may be heat treated for 1 to 28 hours at a temperature of 350 to 500 ° C. More specifically, the homogenization heat treatment may be performed for 18 to 28 hours. If the temperature is too low, it may cause problems that the homogenization is not properly performed and beta phases such as M gl7 Al 12 are not dissolved in the matrix. If the temperature is too high, the beta phases condensed in the casting will melt and cause a fire or vacancy in the magnesium sheet. Therefore, the homogenization heat treatment can be performed within the above-described silver degree range.
  • step S30 the homogeneous cast is warm-rolled.
  • the condition of the silver of warm rolling may be 150 to 350 ° C. If the temperature is too low, a large number of edge cracks may occur. If the temperature is too high, Problems unsuitable for mass production can occur. Therefore, it can be warm-rolled in the above-mentioned silver range.
  • Warm rolling step (S30) can be performed a plurality of times. It can be hot rolled at a reduction rate of 10 to 30% per time. By performing warm rolling a plurality of times, it is possible to finally roll down to a thin thickness of 0.4 nim.
  • the method may further include at least one step of annealing between the plurality of warm rolling pieces.
  • the formability of the magnesium alloy sheet can be further improved.
  • the step of annealing may be carried out at a temperature of 300 to 500 ° C for 1 to 10 hours. More specifically, it can be carried out with a silver of 450 to 500 ° C. In the above-described range, the moldability of the magnesium alloy sheet can be further improved.
  • the method may further include a post heat treatment.
  • a post-heat treatment step the moldability of the magnesium alloy sheet may be further improved.
  • Post-heat treatment may be carried out at 300 to 500 ° C for 1 to 10 hours. In the above-described range, the moldability of the magnesium alloy sheet can be further improved.
  • Method of manufacturing a magnesium alloy sheet according to the embodiment of the present invention for the full 100%, 'Al: 2.7wt% or less than 5wt%, Zn: 0.75wt3 ⁇ 4> than 1M% yihi.
  • a mother alloy containing not less than 0.75% and lwt%, Ca: 0.1% or more and 0.7wt% or less, Mn: more than 0wt% and 1% or less and the remaining unavoidable impurities and magnesium;
  • the master alloy may be a commercially available AZ31 alloy, AL5083 alloy, or a combination thereof. However, it is not limited thereto. Then casting the master alloy to produce a casting material; Can be carried out.
  • the mother alloy may be prepared by dissolving the master alloy in a silver range of 650 to 750 ° C. Thereafter, the molten metal may be cast to manufacture a casting material. At this time, the cast material and the thickness may be 3 to 7mm.
  • the method of manufacturing the cast material die casting, strip casting, billet casting, centrifugal casting, tilt casting, sand casting, direct chill casting (Di rect chil cast cast) or a combination thereof may be used. More specifically, the strip casting method can be used. However, the present invention is not limited thereto.
  • the rolling force may be 0.2t on / mm 2 or more. More specifically, it may be at least lton / mm 2 . More specifically, it may be 1 to 1.5 ton / mm 2 or more.
  • homogenizing heat treatment of the casting material can be carried out. More specifically, homogenizing heat treatment of the casting material; The first heat treatment step in the temperature range of 30CTC magnetically 400 ° C .; And a second heat treatment step in a temperature section at 400 ° C to 500 ° C .; It may include. More specifically, 300 ° C to 400 ° C temperature : the first heat treatment step in the interval; May be performed for 5 hours to 20 hours. In addition, the second heat treatment step in the silver section at 400 ° C to 500 ° C; May be performed for 5 hours to 20 hours.
  • the first heat treatment step in the silver range By performing the first heat treatment step in the silver range, it is possible to remove the Mg-Al-Zn ternary pie phase generated in the casting step. If the ternary pie phase is present, it may adversely affect subsequent processes.
  • the second heat treatment step in the silver range it is possible to release the tension in the slab. In addition, it is possible to more actively induce the recrystallization of the cast structure in the slab.
  • the heat-treated slab may be rolled to a thickness of 0.4 to 3 mm 3 through 1 to 15 rolls. Also. The rolling may be carried out at 15CTC to 350 ° C. ⁇
  • the rolling temperature is less than 150 ° C, it may cause cracks on the surface during rolling, if it exceeds 350 ° C, may not be suitable for the actual production equipment. It can be rolled at 150 ° C to 350 ° C.
  • an intermediate annealing of the rolling material can be carried out.
  • it can be heat-treated for 1 to 15 hours in the range of 300 ° C to 550 ° C silver degree in the interval between the pass and the pass.
  • it can be rolled to the final target thickness by performing annealing once after rolling twice.
  • it can be annealed once and rolled to the final target thickness. More specifically, when annealing the rolled cast material in the above temperature range, it is possible to release the stress generated by the rolling. Therefore, it can roll several times to the thickness of the desired casting material.
  • the skin pass also referred to as temper rolling or temper rolling, means removing the deformation pattern generated in the hot rolled steel sheet after heat treatment, and hot rolling at light pressure to improve hardness.
  • the magnesium alloy sheet produced by performing a skin pass may be rolled at a reduction ratio of 2 to 15% with respect to the thickness of the rolled material, and more specifically, a reduction ratio of 2 to 6%. Can be rolled into. More specifically, when rolling under the silver and pressure conditions, it is possible to secure the moldability because it reduces the development of the (0001) texture, which is a weak base surface texture.
  • the magnesium alloy tube produced by can be rolled at a 2-15% reduction ratio, relative to the rolled slab thickness. More specifically, it may be rolled at a 2 to 6% reduction rate.
  • the reduction ratio it is possible to minimize the change in the texture strength and improve the strength. More specifically, when the reduction ratio is 2 to 6%, the smallest change in the texture strength of the aggregate, the yield strength may be 170 to 300MPa.
  • the limit dome height (LDH) value may be 8 to 9mm.
  • the yield strength may be 250 to 280 MPa, but because the aggregate structure is somewhat developed, the limit dome height (LDH) may be 7 to 8 kPa.
  • LDH limit dome height
  • the area fraction of the twinned structure may be 5% or less with respect to the total area of the magnesium alloy sheet 100%.
  • the area fraction of the twinning structure may be 5 to 20% with respect to the total area of the magnet alloy sheet 100%.
  • black means twinned structure, and as described above, the strength and maintainability of the magnesium alloy sheet may be improved due to the twinning and dislocation.
  • a set of plane (0001) tissue may deteriorate the moldability and again developed. This may be the same phenomenon that occurs when the temperature range during rolling is low. Therefore, the skin pass may be carried out under the temperature range and the reduction ratio according to one embodiment of the present invention.
  • the limit dome height (LDH) in the above is an index for evaluating the formability, in particular, the pressability of the sheet material, can be measured by measuring the deformation height by applying a deformation to the specimen.
  • the limit dome height (LDH) is fixed to the outer peripheral portion of the test piece having a diameter of 50 ⁇ with a force of 10KN, using a spherical punch having a diameter of 20 ⁇ to 5 to 10mm.
  • the strain is applied at a speed of / min to measure the distance that the deviation moves, i.e., the height at which the specimen is deformed until the disc-shaped specimen breaks.
  • A1 3.0 wt%, 0.8 wt.% Zn, 0.6 wt.% Ca, Mn 0.5 comprises a% by weight, and the rest of the cast magnesium passing through the push-down force to the molten metal consisting of Mg and inevitable impurities 1.2ton / mni 2 the two nyaeng gakreul Ash was prepared.
  • Magnesium castings were subjected to homogenization heat treatment at 40CTC for 24 hours, silver rolled at a rolling reduction of 13 ⁇ 4 at 25CTC silver, and then further annealed at 450 ° C for 1 hour, then again at a temperature of 250 ° C. Warm rolling was carried out at a reduction ratio to prepare a magnesium alloy sheet having a final thickness of 0.7 kPa.
  • a magnesium alloy plate was prepared in the same manner as in Example 1 except that A1 3.0 wt% and Zn 0.8 wt% were included.
  • Example 1 In the case of Example 1 (FIG. 2), almost no center segregation was generated in the magnesium alloy plate, whereas in Comparative Example 1 (FIG. 3), it was confirmed that a large amount of center segregation occurred. Such central segregation is a factor that significantly reduces the formability of the magnesium alloy sheet.
  • the secondary el ectron mi croscopy photograph of the magnetite alloy plate prepared in Example 1 is shown in FIG. 4.
  • the white point part of FIG. 4 is Al-Ca secondary phase particle
  • Test Example 2 Measurement of the limit height of the magnet alloy plate
  • the limit copper height is to insert each magnesium alloy sheet material of Examples and Comparative Examples between the upper die and the lower die, and the outer peripheral portion of each test piece with a force of 5 kN. It fixed and the well-known press oil was used. Then, using a spherical punch having a diameter of 30 ⁇ , the strain was applied at a speed of 5 to 10 ⁇ / niin. After the punch was inserted until each test piece broke, the deformation height of each test piece at the time of breaking was determined. The measurement was carried out in a manner.
  • FIG. 5 is a photograph of the result of measuring the limit dome height of the magnesium alloy sheet produced in Example 1.
  • Example 1 The magnesium alloy plates prepared in Example 1 and Comparative Example 1 were shown in FIGS. 6 and 7 by checking the crystal orientations of the respective grains with an X D analyzer.
  • Example 1 In the case of Example 1 (FIG. 6), the contour lines are widely spread, and it can be seen that the crystal orientations of crystal grains in the plate are widely varied. Therefore, it can be confirmed that the moldability of Example 1 is excellent. On the other hand, in the case of Comparative Example K Figure 7), it can be seen that the (0001) peak is concentrated.
  • Example 1 An EBSD photograph of Example 1 was taken and shown in FIG. 8. As shown in ⁇ b>, it can be seen that mi sor i entat i on values are uniformly distributed for each grain, and that each grain has various crystal orientations.
  • A1 3%, Zn: 1%, Ca: 1%, Mn: 0.3%, and the balance prepared a master alloy containing magnesium and unavoidable impurities.
  • the master alloy was cast to prepare a cast material.
  • the cast material was subjected to primary homogenization heat treatment at 350 ° C. for 10 hours.
  • the first homogenized heat treated casting material was subjected to secondary homogenization heat treatment for 450 ° C. for 10 hours.
  • the homogeneous heat-treated casting material was rolled to prepare a rolled material. Thereafter, the rolled material was post-heated at 400 ° C for 10 hours.
  • a magnesium pass plate was manufactured by performing a skin pass on the post-heat-treated rolled material, and the silver pass and rolling reduction are as shown in Table 1 below.
  • Test Example 4 Comparison of mechanical properties according to skin pass reduction rate and silver degree [Table 1] Rolling reduction rate ( ⁇ 3 ⁇ 4 Yield strength (MPa Maximum tensile elongation (% limit Dome height temperature ( ° C)) Strength (MPa)
  • Example 2a 250 5 202 257 22 8.1
  • Table 1 above when the skin pass was carried out on a magnesium alloy having the same composition and composition, it can be seen that the yield strength was improved without a great change in formability. More specifically, moldability can be compared by numerical values of elongation and limit height.
  • the aggregate strength is as disclosed in FIG.
  • Example 3 Compared with 1, the magnet alloy plate was prepared by changing only the conditions disclosed in Table 2 below. As a result, the mechanical properties of the magnesium alloy sheet produced in Example 3 are disclosed in Table 3 below.
  • Non-H Example 3d 8 1 166 4.9 As a result, in the case of Comparative Examples 3a to 3d which did not satisfy the conditions of homogenization annealing time, rolling temperature, and annealing annealing, it was confirmed that moldability was inferior to the present Example. In addition, it can be seen that the yield strength is inferior to the present embodiment. In the case of Comparative Example 3c, it was relatively excellent in moldability compared to other comparative examples with a grain size of 40, but it was less than the present Example.

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Abstract

Un procédé de fabrication d'une tôle en alliage de magnésium selon un mode de réalisation de la présente invention comprend les étapes consistant à : couler du métal en fusion comprenant entre 2,7 et 5 % en poids d'Al, 0,75 à 1 % en poids de Zn, 0,1 à 0,7 % en poids de Ca, 1 % en poids ou moins (0 % exclu) de Mn, et le reste étant Mg et des impuretés inévitables pour préparer un matériau de coulée (S10) ; soumission du matériau de coulée à un traitement thermique d'homogénéisation (S20) ; et laminage à chaud du matériau de coulée homogénéisé (S30).
PCT/KR2016/015228 2015-12-23 2016-12-23 Matériau de tôle d'alliage de magnésium et procédé de fabrication associé WO2017111550A1 (fr)

Priority Applications (4)

Application Number Priority Date Filing Date Title
CN201680075821.9A CN108472699B (zh) 2015-12-23 2016-12-23 镁合金板材及其制造方法
JP2018532629A JP6758383B2 (ja) 2015-12-23 2016-12-23 マグネシウム合金板材、およびその製造方法
EP16879417.0A EP3395458B1 (fr) 2015-12-23 2016-12-23 Matériau de tôle d'alliage de magnésium et procédé de fabrication associé
US16/065,562 US20190093200A1 (en) 2015-12-23 2016-12-23 Magnesium alloy sheet and method for manufacturing same

Applications Claiming Priority (4)

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

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WO2017111550A1 true WO2017111550A1 (fr) 2017-06-29
WO2017111550A8 WO2017111550A8 (fr) 2017-09-28

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Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108796327A (zh) * 2018-06-28 2018-11-13 郑州大学 一种高塑性、低各向异性变形镁合金板材及其制备方法
KR20200075567A (ko) * 2018-12-18 2020-06-26 주식회사 포스코 성형성이 우수한 마그네슘 합금 판재의 제조방법 및 이로부터 제조된 마그네슘 합금 판재
JP2021508002A (ja) * 2017-12-26 2021-02-25 ポスコＰｏｓｃｏ マグネシウム合金板材およびその製造方法
JP2021508003A (ja) * 2017-12-26 2021-02-25 ポスコＰｏｓｃｏ マグネシウム合金板材およびその製造方法
CN113416873A (zh) * 2021-06-28 2021-09-21 晋中学院 高电磁屏蔽效能稀土镁合金板材及其制备方法
CN113770175A (zh) * 2021-09-30 2021-12-10 重庆大学 一种低温大道次压下量轧制无边裂镁合金板材的方法

Families Citing this family (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20190000676A (ko) * 2017-06-23 2019-01-03 주식회사 포스코 마그네슘 합금 판재 및 이의 제조방법
US20220275477A1 (en) * 2019-08-26 2022-09-01 Ohio State Innovation Foundation Magnesium alloy based objects and methods of making and use thereof
CN113005347B (zh) * 2021-02-25 2021-10-08 吉林大学 一种高塑性Mg-Al-Ca镁合金及其制备方法

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2009007606A (ja) * 2007-06-27 2009-01-15 Mitsubishi Alum Co Ltd 耐食性及び表面処理性に優れるマグネシウム合金板材とその製造方法
JP2010229467A (ja) * 2009-03-26 2010-10-14 Hitachi Metals Ltd マグネシウム合金薄板の製造方法
KR101078308B1 (ko) * 2008-05-19 2011-10-31 포항공과대학교 산학협력단 고강도 마그네슘 합금 판재 및 그 제조방법
KR101481909B1 (ko) * 2013-08-08 2015-01-13 주식회사 포스코 마그네슘 합금의 제조 방법
KR20150065418A (ko) * 2013-12-05 2015-06-15 주식회사 포스코 마그네슘 합금 판재 및 이의 제조 방법

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2010156007A (ja) * 2008-12-26 2010-07-15 Mitsubishi Alum Co Ltd 耐食性及び表面処理性に優れるマグネシウム合金板材とその製造方法
JP5424391B2 (ja) * 2009-09-30 2014-02-26 国立大学法人長岡技術科学大学 マグネシウム合金圧延材並びにその製造方法
JP5590660B2 (ja) * 2010-03-01 2014-09-17 独立行政法人産業技術総合研究所 冷間成形性と面内異方性を改善したマグネシウム合金板材及びその作製方法
JP5660525B2 (ja) * 2010-03-05 2015-01-28 独立行政法人産業技術総合研究所 アルミニウム合金並みの常温成形性を発揮する汎用マグネシウム合金板材及びその製造方法

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2009007606A (ja) * 2007-06-27 2009-01-15 Mitsubishi Alum Co Ltd 耐食性及び表面処理性に優れるマグネシウム合金板材とその製造方法
KR101078308B1 (ko) * 2008-05-19 2011-10-31 포항공과대학교 산학협력단 고강도 마그네슘 합금 판재 및 그 제조방법
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
KR101481909B1 (ko) * 2013-08-08 2015-01-13 주식회사 포스코 마그네슘 합금의 제조 방법
KR20150065418A (ko) * 2013-12-05 2015-06-15 주식회사 포스코 마그네슘 합금 판재 및 이의 제조 방법

Cited By (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2021508002A (ja) * 2017-12-26 2021-02-25 ポスコＰｏｓｃｏ マグネシウム合金板材およびその製造方法
JP2021508003A (ja) * 2017-12-26 2021-02-25 ポスコＰｏｓｃｏ マグネシウム合金板材およびその製造方法
EP3733889A4 (fr) * 2017-12-26 2021-03-03 Posco Feuille d'alliage de magnésium et procédé pour sa fabrication
US11773472B2 (en) 2017-12-26 2023-10-03 Posco Co., Ltd Magnesium alloy sheet and method for producing same
CN108796327A (zh) * 2018-06-28 2018-11-13 郑州大学 一种高塑性、低各向异性变形镁合金板材及其制备方法
KR20200075567A (ko) * 2018-12-18 2020-06-26 주식회사 포스코 성형성이 우수한 마그네슘 합금 판재의 제조방법 및 이로부터 제조된 마그네슘 합금 판재
KR102239185B1 (ko) * 2018-12-18 2021-04-12 주식회사 포스코 성형성이 우수한 마그네슘 합금 판재의 제조방법 및 이로부터 제조된 마그네슘 합금 판재
CN113416873A (zh) * 2021-06-28 2021-09-21 晋中学院 高电磁屏蔽效能稀土镁合金板材及其制备方法
CN113770175A (zh) * 2021-09-30 2021-12-10 重庆大学 一种低温大道次压下量轧制无边裂镁合金板材的方法

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CN108472699A (zh) 2018-08-31
CN108472699B (zh) 2021-12-28
JP2019504207A (ja) 2019-02-14
JP6758383B2 (ja) 2020-09-23
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WO2017111550A8 (fr) 2017-09-28
EP3395458A4 (fr) 2018-10-31

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