JP4991280B2 - Magnesium alloy sheet manufacturing method - Google Patents

Description

  The present invention relates to a method for producing a magnesium alloy thin plate having a uniform fine crystal grain structure obtained by a warm different peripheral speed rolling process of a twin roll method.

  It is well known that the mechanical properties of magnesium alloys are strongly dependent on the crystal grain size, and that they have various excellent properties, such as the finer the crystal grains, the higher the strength and elongation, and the easier superplasticity appears. It has been. Conventionally, as a method for producing a magnesium alloy plate having a fine crystal grain structure, a thermomechanical processing method is often used. This method controls the dynamic recrystallization phenomenon during hot working, or the solid solution, precipitation phenomenon, recovery and recrystallization phenomenon of solute elements during the heat treatment during and / or after warm working. In many cases, the above-mentioned phenomena are comprehensively controlled to refine crystal grains. Recently, a high strain processing method such as ECAP (Equal channel angular pressing) has been developed.

  However, since the crystal structure of the magnesium alloy is a dense hexagonal crystal, it is difficult to be plastically deformed at room temperature, and cold workability is poor. Therefore, in the conventional manufacturing method from a thick slab, heating and hot or warm Since the rolling at is repeated, the size of the crystal grain of the magnesium alloy plate obtained even when the heat treatment method is applied is limited to about 10 μm. In addition, a strong strain processing method such as ECAP is still a laboratory level technique and cannot be applied as a mass production technique for magnesium alloy sheets.

  Furthermore, in the conventional method described above, since heating and rolling for producing a magnesium alloy sheet having a predetermined thickness are repeated, a great amount of time and labor are required, which hinders improvement in productivity. This was also reflected in the manufacturing cost of the magnesium alloy sheet.

  In view of the above circumstances, in Patent Document 1, in a magnesium alloy sheet manufacturing process, a technique of obtaining a fine crystal grain structure having an average grain diameter of 5 μm or less by introducing a warm different peripheral speed rolling process into a twin roll method. Is disclosed.

However, only by introducing the above process, a change in the setting requirements of the warm different peripheral speed rolling process may result in a case where the average grain size does not become 5 μm or less, or a fine grain structure having an average grain size of 5 μm or less. There were cases where it was limited in part. In addition, the need to reduce the average grain size to 4 μm or less has been increasing due to the mechanical properties of magnesium alloys, where the crystal grains become finer and the strength and elongation improve and superplasticity tends to appear.
JP 2006-144062 A

  The present invention has been made in view of the above circumstances, and is a method for producing a magnesium alloy thin plate having a uniform and fine crystal grain structure with an average grain size of 4 μm or less, quickly and stably, with low material and production costs. The purpose is to provide.

In order to achieve the above object, the present invention employs the following configuration. That is, the magnesium alloy thin plate manufacturing method of the present invention is in mass%, Al: 1.0 to 11%, Zn: 2.0% or less, Mn: 0.1 to 0.5%, the balance being Mg and inevitable. The molten magnesium alloy containing impurities is continuously cast and rolled to form a strip, and then homogenization, hot rolling and intermediate annealing are performed in this order, or hot rolling and homogenization are performed in this order. In the manufacturing method of the magnesium alloy thin plate which performs warm rolling after performing, in part or all of the said warm rolling, material heating temperature shall be the range of 200 to 280 degreeC, and roll roll surface temperature will be 180 to 280 degreeC. It is characterized by carrying out warm different peripheral speed rolling with a rolling reduction of 15% or more under the condition of a rotational peripheral speed ratio of 1.1 to 1.7 of the upper and lower rolls.

  According to said structure, the magnesium alloy thin plate which has a uniform fine crystal grain structure | tissue whose average particle diameter is 4 micrometers or less can be manufactured quickly and stably with a low material and manufacturing cost. Furthermore, a magnesium alloy sheet suitable for applications requiring strength, ductility, superplasticity and the like can be obtained. Moreover, since the magnesium alloy thin plate manufactured by this invention has a fine crystal grain, it is excellent in a moldability.

Hereinafter, the manufacturing method of the magnesium alloy thin plate of this invention is demonstrated.
FIG. 1 shows an example of an embodiment of a method for producing a magnesium alloy sheet according to the present invention. First, a molten magnesium alloy, the continuous casting and rolling S ₁ by a twin roll method, to produce a cast strip having a strip. The plate thickness of the cast plate is 2 to 10 mm.

The continuous casting and rolling S ₁ is the molten magnesium alloy, a step of casting and rolling to continuously thin strip-shaped plate. The continuous casting and rolling S _1, the production of magnesium alloy sheet is extremely efficient.

  As a continuous casting and rolling method, a twin roll method is preferable. The twin roll method is a method in which molten magnesium alloy obtained in a melting furnace is supplied to a tundish, and the molten magnesium alloy supplied from the tundish is supplied between water-cooled twin rolls and rolled. However, the continuous casting and rolling method is not limited to the twin roll method.

  Fig.2 (a) is the schematic of the rolling part of a twin roll apparatus. The rolling unit of the twin roll device is composed of a twin roll unit 1 and a blowing nozzle 10. The twin roll unit 1 includes an upper roll 2 and a lower roll 3, two release agent sprays 4, and a roll surface temperature sensor 5. A magnesium alloy melt is supplied between the twin rolls cooled by water from the blowing nozzle 10 to produce a cast plate. The roll surface temperature is measured by the roll surface temperature sensor 5. After rolling, the surfaces of the upper roll 2 and the lower roll 3 are cleaned with a release agent spray 4.

FIG. 2B is an enlarged schematic diagram of the blowing nozzle 10 in the schematic diagram. The blowing nozzle 10 includes a tip part 11 and a trough part 12. The space above the trough portion 12 is filled with an inert gas such as SF ₆ + N ₂ flowing from the gas pipe 15. The laser level is irradiated from the laser level level sensor 16 through the heat-resistant glass 17, and the reflected light on the level is again measured by the laser level level sensor 16 to measure the level of the level. . Based on the measurement result, the molten magnesium alloy is replenished through the transfer pipe 14. The temperature of the magnesium alloy molten metal 13 is measured by two thermocouples 18. Supply of the molten magnesium alloy to the twin rolls is performed from the tip portion 11.

  As the magnesium alloy molten metal, a magnesium alloy containing Al, Zn, and Mn and the balance of Mg and inevitable impurities is used.

  The Al is preferably added in the range of 1.0 to 11%, and more preferably in the range of 2.0 to 4.0%. The Al is actively added for the purpose of improving mechanical properties such as castability and strength, and corrosion resistance. However, if the amount of Al exceeds 11%, the workability in the rolling process decreases. To do. Further, when the addition amount of Al is less than 1.0%, sufficient castability, strength and corrosion resistance cannot be obtained.

  Zn may be added within a range of 2.0% or less. Zn, like Al, contributes to improvement of mechanical properties such as castability and strength. However, if the amount of Zn exceeds 2.0%, castability deteriorates.

  The Mn is preferably added within a range of 0.1 to 0.5%. The Mn has an effect of alleviating the influence of elements that lower the corrosion resistance. That is, by adding Mn, the influence of Fe, which is an impurity element that lowers corrosion resistance, can be mitigated, and by adding it within the above range, the effect can be most exerted. If it exceeds 5%, a coarse intermetallic compound is produced during continuous casting and rolling, and the rollability deteriorates.

Next, as shown in FIG. 1, homogenization treatment S ₂ , hot rolling S ₃ , and intermediate annealing S ₄ are performed in this order, or hot rolling S ₅ and homogenization treatment S ₆ are performed in this order. A magnesium alloy plate is manufactured from the cast plate.

The homogenization treatments S ₂ and S ₆ are steps of heat-treating the cast plate under certain conditions. As for the said conditions, the heat processing hold | maintained in the temperature range of 370 degreeC-470 degreeC for 1 hour or more is preferable. The solute elements such as Al and Zn rapidly solidified in the continuous casting and rolling S ₁ are segregated at a high concentration at the dendrite cell boundary and the central portion of the plate thickness. However, the solute is subjected to the homogenization treatments S ₂ and S _6. This is because high concentration segregation of elements can be eliminated. Moreover, it can also be set as the magnesium alloy plate excellent in rolling property.

The hot rolling S ₃ and S ₅ are rolling processes in which the cast plate is a magnesium alloy plate under certain conditions. As for the said conditions, it is preferable that the material heating temperature shall be 280-350 degreeC, and the roll surface temperature of a rolling apparatus shall be the range of 150-350 degreeC.

The intermediate annealing S _4, under certain conditions, a step of heat-treating the magnesium alloy plate. Examples of the conditions include heat treatment that is held for 1 to 8 hours in a temperature range of 300 to 350 ° C., heat treatment that is held for 1 minute or less in a temperature range of 350 to 450 ° C. Furnace for use in the intermediate annealing S ₄ is batch furnace may be any of a continuous furnace.

Finally, as shown in FIG. 1, it performs a differential speed rolling S ₇ warm, to produce magnesium alloy sheet of the magnesium alloy plate.

The warm differential speed rolling S _7, under certain conditions, a rolling step for the magnesium alloy plate and magnesium alloy thin plate. The material heating temperature is in the range of 200 ° C. to 280 ° C., the roll surface temperature of the rolling apparatus is in the range of 180 to 280 ° C., and the rotational peripheral speed ratio between the upper and lower rolls of the different peripheral speed rolling mill (hereinafter referred to as peripheral speed). The ratio is preferably 1.1 to 1.7. The rolling reduction is preferably 15% or more. The configuration of the differential speed rolling mill to perform the differential speed rolling S ₇ warm is not limited in particular, it is possible to use known devices.

In the warm differential speed rolling S _7, if the peripheral speed ratio is smaller than 1.1, sufficient additional shear deformation because not obtained, not obtained fine grain structure. Further, the effect of refining crystal grains is low, and a mixed grain structure in which coarse crystal grains are present in some places is obtained.

  In the region where the peripheral speed ratio is 1.1 or more, the crystal grain size can be made finer as the peripheral speed ratio increases. However, when the peripheral speed ratio is 1.7, the effect of crystal grain refinement is achieved. Is saturated. If the peripheral speed ratio is greater than 1.7, not only the effect on crystal grain refinement will not be improved, but also the magnesium alloy sheet may be easily damaged during rolling.

  When the material heating temperature during the warm different peripheral speed rolling exceeds 280 ° C., grain growth during rolling becomes significant, and the average grain size may exceed 4 μm. Therefore, in obtaining a fine grain structure It is not preferable. Similarly, when the roll surface temperature during the warm different peripheral speed rolling exceeds 280 ° C., grain growth during rolling becomes significant, and the average grain size may exceed 4 μm. It is not preferable in obtaining.

  If the minimum value of the roll surface temperature at the time of the warm different peripheral speed rolling is set to 180 ° C. and the minimum value of the material heating temperature is set to 200 ° C., even if the roll at the time of rolling performs heat removal of the material temperature, the material Since the temperature is 180 ° C. or higher and the dynamic recrystallization temperature is 180 ° C. or higher, dynamic recrystallization is caused and crystal grains of the magnesium alloy plate are refined. When the roll surface temperature at the time of the warm different peripheral speed rolling is less than 180 ° C., dynamic recrystallization is not caused, and the crystal grain refinement of the magnesium alloy sheet is also not performed.

  When the rolling reduction is less than 15%, sufficient shear strain cannot be obtained, so that the crystal grains do not become fine.

Incidentally, the warm differential speed rolling S ₇ is may be performed as part of a warm rolling. The warm rolling is a rolling process in which a magnesium alloy sheet is made into a magnesium alloy sheet under certain conditions. As for the said conditions, it is preferable to make material heating temperature into the range of 200-280 degreeC, and roll surface temperature of a rolling mill into the range of 180-280 degreeC.

In the warm differential speed rolling S ₇ or the warm rolling, number of passes may be the one, it may be a plurality of times. However, the rolling reduction per pass is preferably 30% or more. As the rolling reduction in the final warm different peripheral speed rolling or the final warm rolling, a rolling reduction of 50% or more is particularly preferable. The rolling reduction may be a single rolling or a plurality of rollings.

The intermediate annealing S _4, may be provided in the middle of the warm rolling. In particular, if the rolling reduction in the warm rolling is more than 80%, to provide an intermediate annealing S ₄ are preferred. Even rolling reduction in one warm rolling is 80% or less, when the total rolling reduction at twice or more warm rolling is more than 80%, to perform intermediate annealing S ₄ on the way Is preferred.

  Further, depending on the required specifications of the product, after the warm rolling, cold rolling and annealing may be further combined, or may be performed independently.

Hereinafter, effects of the embodiment of the present invention will be described.
The manufacturing method of the magnesium alloy sheet of the present invention is, in mass%, Al: 1.0 to 11%, Zn: 2.0% or less, Mn: 0.1 to 0.5%, the balance being Mg and inevitable impurities. Using the molten magnesium alloy contained, continuous casting and rolling are performed to form strips, and then homogenization, hot rolling, and intermediate annealing are performed in this order, or hot rolling and homogenization are performed in this order. After that, it is a method of manufacturing a magnesium alloy sheet that is warm-rolled, so that each process can be performed quickly and stably, and the materials and manufacturing costs can be reduced by operating each process appropriately. Can do.

  The method for producing a magnesium alloy sheet according to the present invention includes a material heating temperature in a range of 200 ° C. to 280 ° C. and a roll surface temperature of a rolling device in a range of 180 to 280 ° C. Since it is a structure characterized by performing the warm different peripheral speed rolling under the condition of the rotational peripheral speed ratio of the roll of 1.1 to 1.7, in the warm different peripheral speed rolling, dynamic recrystallization is performed and 4 μm. It can be set as the magnesium alloy thin plate which consists of the following fine crystal grain structures, and it can be set as the magnesium alloy thin plate suitable for the use as which intensity | strength, ductility, superplasticity, etc. are requested | required.

  Hereinafter, the present invention will be specifically described based on examples. However, the present invention is not limited only to these examples.

Example 1
Using the magnesium alloy plate, a magnesium cast plate having a thickness of 5.4 mm was manufactured by a twin roll method. Table 1 shows chemical components of the magnesium alloy sheet.

  Next, the magnesium cast plate of the alloy 1 was subjected to a homogenization treatment that was held at a temperature of 450 ° C. for 8 hours in an argon gas atmosphere. Furthermore, hot rolling was performed under conditions of a material heating temperature of 300 ° C. and a roll temperature of 200 ° C., and the thickness of the magnesium cast plate was 2.1 mm. Finally, the intermediate annealing which hold | maintains at the temperature of 300 degreeC for 1 hour was performed, and the 2.1 mm-thick magnesium alloy plate was manufactured.

  The magnesium alloy sheet was set in a different peripheral speed rolling mill, and warm different peripheral speed rolling was performed. The different peripheral speed rolling mill used a twin motor drive type in which a heater was built in a roll. Here, the peripheral speed on the high speed upper roll side was 8 m / min, the peripheral speed on the lower roll side was 5.3 m / min, and the peripheral speed ratio was set to 1.50. The roll surface temperature was 250 ° C., and rolling was repeated until the target plate thickness was 0.8 mm to produce a magnesium alloy thin plate having a plate thickness of 0.8 mm. Moreover, the said magnesium alloy plate was heated at 250 degreeC with the heat processing furnace for every time (1 pass). Moreover, the direction of warm different circumferential speed rolling was set to be constant.

The magnesium alloy thin plate was observed with an optical microscope and evaluated for tensile properties.
The optical microscope observation was performed with a cross section parallel to the rolling direction. The observation surface of the optical microscope was polished with Emery # 1000, and then etched with a mixed solution of 20 ml of distilled water, 32 ml of picric acid, 18 ml of ethyl alcohol, and 20 ml of glacial acetic acid for 20 seconds. The crystal grain size was measured by a cutting method.
The tensile property evaluation was performed using a tensile test piece obtained by cutting the prepared magnesium alloy thin plate in the rolling direction. The size of the tensile test piece was a parallel part length 30 mm × width 12.5 mm × thickness 0.8 mm, and the tensile test conditions were a strain rate of 3.3 × 10 ⁻³ / sec at room temperature.
Examples 2 to 4 and Comparative Example 1 are as shown in Table 2.

(Example 5)
A magnesium alloy sheet was produced in the same manner as in Example 1 except that the roll surface temperature in the warm different peripheral speed rolling was set to 200 ° C. Observation with an optical microscope was performed in the same manner as in Example 1.

(Comparative Example 2)
A magnesium alloy sheet was produced in the same manner as in Example 1 except that the roll surface temperature in the warm different peripheral speed rolling was set to 150 ° C. Observation with an optical microscope was performed in the same manner as in Example 1.

  The results of Example 1, Example 5 and Comparative Example 2 are shown in Table 3.

  The present invention relates to a magnesium alloy thin plate having a uniform and fine crystal grain structure having an average grain size of 4 μm or less, using a twin roll method of warm differential rolling at a low speed and with a low material and manufacturing cost. There is an applicability in the industrial field that requires a method of manufacturing In addition, it can be used in application fields that require a magnesium alloy sheet having strength, elongation, and superplasticity.

It is a figure explaining an example of the manufacturing method of the magnesium alloy thin plate which is embodiment of this invention. It is a figure explaining an example of the manufacturing method of the magnesium alloy thin plate which is embodiment of this invention, Comprising: (a) is the schematic of the rolling part of a twin roll method. (B) is an enlarged schematic diagram of a blowing nozzle.

Explanation of symbols

DESCRIPTION OF SYMBOLS 1 ... Twin roll part, 2 ... Upper roll, 3 ... Lower roll, 4 ... Release agent spray, 5 ... Roll surface temperature sensor, 10 ... Blowing nozzle, 11 ... Tip part, 12 ... Trough part, 13 ... Molten metal, 14 ... transfer pipe, 15 ... inert gas, 16 ... laser type hot water level sensor, 17 ... heat resistant glass, 18 ... thermocouple, S1 ... continuous casting and rolling, S2 ... homogenization treatment, S3 ... hot rolling, S4 ... Intermediate annealing, S5 ... Hot rolling, S6 ... Homogenization treatment, S7 ... Different peripheral speed warm rolling

Claims (1)

In mass%, Al: 1.0 to 11%, Zn: 2.0% or less, Mn: 0.1 to 0.5%, the remaining magnesium alloy containing Mg and inevitable impurities is continuously cast and rolled. After performing the strip-shaped plate, homogenization treatment, hot rolling, and intermediate annealing are performed in this order, or after hot rolling and homogenization processing are performed in this order, the material heating temperature is 200 ° C. to 280 ° C. The rolling roll surface temperature is in the range of 180 to 280 ° C., and the different rolling speeds are set to 15% or more under the condition of the rotational circumferential speed ratio of 1.1 to 1.7 of the upper and lower rolls. A method for producing a magnesium alloy sheet.

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