WO2015155911A1 - 曲げ加工性と形状凍結性に優れた高強度アルミニウム合金板およびその製造方法 - Google Patents
曲げ加工性と形状凍結性に優れた高強度アルミニウム合金板およびその製造方法 Download PDFInfo
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- 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
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
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- 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
Definitions
- the present invention relates to a 3000 series aluminum alloy plate excellent in bending workability and shape freezing property, which is used for body panels for automobiles.
- an aluminum alloy plate As a body sheet for automobiles, it is necessary to form it into a desired shape with a press mold, and a 5000 series aluminum alloy plate excellent in press formability with controlled texture is developed. It has been.
- the 5000 series aluminum alloy plate has been used as a body sheet material for automobiles because it has high strength because Mg dissolves in the matrix and has excellent press formability by controlling the texture. .
- Patent Document 1 is an Al—Mg-based alloy plate containing 2 wt% ⁇ Mg ⁇ 6 wt% of Mg, and summing at least one selected from Fe, Mn, Cr, Zr, and Cu. 0.03 wt% or more (when Cu is selected, 0.2 wt% or more as Cu), and the upper limit of the content of each element is Fe ⁇ 0.2 wt%, Mn ⁇ 0.6 wt%, Cr ⁇ 0.3 wt%, Zr ⁇ 0.3 wt%, Cu ⁇ 1.0%, with the balance being Al and inevitable impurities, the ratio of the volume fraction of CUBE orientation to the volume fraction of S orientation ( Al / Mg-based alloy sheet having an excellent deep-drawing formability, having a texture with S / Cube) of 1 or more and a GOSS orientation of 5% or less and a crystal grain size in the range of 20 to 100 ⁇ m Has been developed.
- Patent Document 2 discloses that the orientation density of the CR orientation ( ⁇ 001 ⁇ ⁇ 520>, the same applies hereinafter) is any orientation other than the CR orientation for the texture of aluminum or an aluminum alloy plate (hereinafter, aluminum alloy plate).
- An aluminum alloy plate for press molding characterized in that its component composition is, for example, Si: 0.2% to 2.0% (mass%, the same applies hereinafter), Mg: 0 2% to 1.5%, Cu: 1.0% or less, Zn: 0.5% or less, Fe: 0.5% or less, Mn: 0.3% or less, Cr: 0.
- Patent Document 3 includes Mg 0.3 to 2.0% (mass%, the same shall apply hereinafter) and Si 0.3 to 2.5%, with the balance being Al and inevitable impurities.
- Al—Mg—Si alloy plate that has been subjected to a heat treatment, wherein the ⁇ 432 ⁇ plane is within 9.0 ° from the parallel to the plate surface with respect to the total grain area of all crystal orientations
- the area ratio is 0.15 or more, and the highest one of the azimuth distribution functions of azimuths consisting of ⁇ 111 ⁇ ⁇ 112>, ⁇ 332 ⁇ ⁇ 113>, ⁇ 221 ⁇ ⁇ 114>, and ⁇ 221 ⁇ ⁇ 122> ⁇ / ⁇ is 2.0 or more and the average rankford value is 0.9 or more, where ⁇ is ⁇ and the higher one of the orientation distribution functions of ⁇ 001 ⁇ ⁇ 100> and ⁇ 001 ⁇ ⁇ 110> is ⁇ .
- a highly formable Al—Mg—Si based alloy sheet is described. According to this, rough rolling is performed on the ingot at a temperature of 150 ° C. or higher and in a non-recrystallization temperature range at a reduction ratio of more than 50%, and at a temperature of 150 ° C. or higher and in a non-recrystallization temperature range,
- the recrystallization texture as described above can be obtained by carrying out rolling at a speed ratio of 1.2 to 4.0 at a reduction ratio of more than 50% to obtain a final sheet thickness, followed by solution treatment. That's it.
- the body sheet for automobiles needs to be subjected to hem bending in order to crimp and integrate the outer panel and the inner panel.
- the 6000 series aluminum alloy plate is inferior to the 5000 series aluminum alloy plate in so-called bending workability, it is necessary to prevent microcracking and rough skin after bending.
- defects such as microcracks which are considered to be caused by the formation of high-density shear bands, are often observed, and it is also a problem to appropriately control the recrystallized texture.
- Non-Patent Document 1 a single crystal is produced using an Al—Mg—Si alloy sheet as a test material, and the influence of each crystal orientation on bending workability is investigated in detail from the viewpoint of shear band formation. According to this investigation, it is clear that there is a close relationship between the crystal orientation and the bending workability. Among the investigations, the bending workability of the test piece having the ⁇ 001> // ND orientation is the highest. It was good and the bending anisotropy was the smallest.
- Patent Document 4 contains Fe in an amount of 1.0 to 2.0% by mass and Mn in an amount of 2.0% by mass or less, and the balance is made of aluminum and unavoidable impurities.
- Excellent in formability characterized by having a component composition limited to 01% by mass or less, an average crystal grain size of 20 ⁇ m or less, and a structure in which the area ratio of ⁇ 110 ⁇ -oriented crystals is adjusted to 25% or more Aluminum alloy sheets are described. According to this, 35% or more elongation, 0.85 or more average r-value, 33 mm or more ball head overhang height, and a limit drawing ratio of 2.17 or more are all obtained by DC casting with electromagnetic stirring. It can be achieved.
- 5000 series and 6000 series aluminum alloy plates are excellent in formability and have characteristics as body sheets for automobiles.
- the oxide film produced on the surface is relatively thick, and surface treatment such as pickling may be required before press molding.
- a surface pattern such as a stretcher / strain mark or ridging may occur during press molding.
- the mechanical properties of the 6000 series aluminum alloy plate may change over time due to natural aging after the final plate is manufactured.
- Patent Document 4 describes 3000-series and 8000-series aluminum alloy plates that do not contain Mg as an essential element. After both faces of the resulting ingot are chamfered, homogenized heat treatment, rolling process is performed. It was necessary to perform final annealing, and the number of processes was large and the cost was high.
- the present invention has been devised to solve such problems, has high strength applicable to automobile body sheets, and is a recrystallized aggregate obtained by annealing a rolling texture.
- An object of the present invention is to provide a 3000 series aluminum alloy plate having an adjusted structure and excellent formability, particularly bending workability and shape freezing property.
- the high-strength aluminum alloy sheet having excellent formability has Mn: 1.0 to 1.6% by mass, Fe: 0.1 to 0.8% by mass, Si: 0 .5 to 1.0% by mass, Ti: 0.005 to 0.10% by mass, Mg as an impurity is regulated to less than 0.10% by mass, and the balance is composed of Al and inevitable impurities
- the metal structure has an area ratio of the second phase particles having an equivalent circle diameter of 1 ⁇ m or more of 1.5 to 3.5%, an average crystal grain size of 20 to 50 ⁇ m, and parallel to the plate surface ⁇ 100 ⁇ Recrystallized aggregate in which the ratio of AR ⁇ 100 ⁇ / AR ⁇ 123 ⁇ ⁇ 634>, which is the ratio of the area ratio of the orientation crystal and the area ratio of the ⁇ 123 ⁇ ⁇ 634> orientation crystal parallel to the plate surface, is 4.8 or more While exhibiting a structure, tensile strength 155 MPa or more, 0.2% proof stress 100 MPa or less,
- the high-strength aluminum alloy plate excellent in formability and shape freezing property of the present invention is obtained by continuously casting a slab having a thickness of 2 to 15 mm by using a thin slab continuous casting machine using a molten aluminum alloy having the above-described composition.
- the slab is manufactured by winding directly on a roll without hot rolling, then cold rolling, cold rolling with a final cold rolling rate of 70 to 95%, and then final annealing. .
- As the final annealing it is desirable to perform continuous annealing at a holding temperature of 450 to 560 ° C. for 10 to 60 seconds.
- the aluminum alloy plate of the present invention has high strength, high elongation value, and relatively low yield strength, so that spring back during press forming is suppressed, and as a result, shape freezing property is excellent.
- the recrystallized texture is a ratio of the area ratio of ⁇ 100 ⁇ -oriented crystals parallel to the plate surface to the area ratio of ⁇ 123 ⁇ ⁇ 634> -oriented crystals parallel to the plate surface, AR ⁇ 100 ⁇ / AR Since ⁇ 123 ⁇ ⁇ 634> is 4.8 or more, it is particularly excellent in bending workability.
- a high-strength aluminum alloy plate excellent in formability and shape freezing that can be applied to an automobile body panel or the like is provided at a low price.
- the conventional 3000 series aluminum alloy plate has high strength, there are many cases where defects such as microcracking and rough appearance occur especially in bending. For this reason, it is necessary to appropriately control the recrystallized texture and appropriately adjust the recrystallized grain size and crystal orientation.
- the 3000 series aluminum alloy sheet has a high yield strength depending on its component composition or manufacturing process, so that a springback is likely to occur after press molding, and it does not fit into a predetermined design shape. There is also a problem.
- the 3000 series aluminum alloy sheet may have a rough surface appearance after press molding or bending. Therefore, a material to be used is required to have high strength, high elongation, low yield strength, and appropriately controlled recrystallization texture.
- Mn 1.0 to 1.6% by mass
- Mn is an element that increases the strength of the aluminum alloy plate, and a part of the element is an essential element because it partly dissolves in the matrix and promotes solid solution strengthening.
- Mn is also an element constituting a fine intermetallic compound such as Al— (Fe ⁇ Mn) —Si at the time of casting within the range of the alloy composition of the present invention, and further dissolved in the matrix at the time of final annealing.
- the Mn that has been deposited also precipitates as a fine intermetallic compound, increasing the strength.
- the Mn content exceeds 1.6% by mass, the yield strength of the aluminum alloy plate becomes too high, and the shape freezing property at the time of press molding is lowered, which is not preferable. Furthermore, the temperature required for recrystallization during the final annealing becomes too high, which is not preferable because the productivity is lowered. Moreover, when the Mn content is less than 1.0% by mass, the strength of the aluminum alloy plate becomes too low, which is not preferable.
- the preferable Mn content is in the range of 1.0 to 1.6% by mass.
- a more preferable Mn content is in the range of 1.05 to 1.6% by mass.
- a more preferable Mn content is in the range of 1.1 to 1.6% by mass.
- Fe 0.1 to 0.8% by mass
- fine intermetallic compounds such as Al— (Fe ⁇ Mn) —Si are crystallized to increase the strength of the aluminum alloy plate.
- a part of Mn dissolved in the matrix is diffused and absorbed by these intermetallic compounds, so that the yield strength of the final annealed plate is reduced and the elongation is increased. Since these fine intermetallic compounds act as nuclei of recrystallized grains at the time of final annealing, and can adjust the crystal grain size of recrystallization to a predetermined range, it is possible to prevent rough skin after press molding, It is an essential element.
- the size and number of intermetallic compounds such as Al— (Fe ⁇ Mn) —Si are decreased, and the area ratio of the second phase particles is decreased.
- the effect of refining crystal grains is weakened, and a predetermined recrystallized structure cannot be obtained due to the action of preventing recrystallization of Mn solid-solved in the matrix.
- the size and number of intermetallic compounds such as Al— (Fe ⁇ Mn) —Si increase, resulting in an increase in the area ratio of the second phase particles and the final annealing.
- the amount of Mn solid solution in the matrix sometimes decreases and the elongation is high and the proof stress is low, the strength is lowered, which is not preferable.
- the Fe content is in the range of 0.1 to 0.8% by mass.
- a more preferable Fe content is in the range of 0.1 to 0.7% by mass.
- a more preferable Fe content is in the range of 0.15 to 0.6% by mass.
- Si 0.5 to 1.0% by mass
- fine intermetallic compounds such as Al— (Fe ⁇ Mn) —Si are crystallized to increase the strength of the aluminum alloy plate.
- a part dissolves in the matrix to increase the strength.
- a part of Mn dissolved in the matrix is diffused and absorbed by these intermetallic compounds, so that the yield strength of the final annealing plate is reduced and the elongation is increased.
- these fine intermetallic compounds act as nuclei of recrystallized grains at the time of final annealing, and can adjust the crystal grain size of recrystallization to a predetermined range, it is possible to prevent rough skin after press molding, It is an essential element.
- the Si content is less than 0.5% by mass, the size and number of intermetallic compounds such as Al— (Fe ⁇ Mn) —Si are reduced, thereby reducing the area ratio of the second phase particles. Since the amount of Si dissolved in the matrix also decreases, a predetermined strength cannot be obtained, which is not preferable. If the Si content exceeds 1.0% by mass, the strength of the aluminum alloy plate increases, but the elongation decreases and the formability decreases, which is not preferable.
- the Si content is in the range of 0.5 to 1.0% by mass.
- a more preferable Si content is in the range of 0.55 to 1.0 mass%.
- a more preferable Si content is in the range of 0.6 to 1.0% by mass.
- Ti 0.005 to 0.10% by mass Ti is an essential element because it acts as a grain refiner during ingot casting and can prevent casting cracks.
- Ti may be added alone, but when coexisting with B, a more powerful grain refinement effect can be expected, so addition with a rod hardener such as Al-5% Ti-1% B There may be.
- the Ti content is less than 0.005% by mass, the effect of miniaturization at the time of ingot casting is insufficient, which may cause casting cracks, which is not preferable. If the Ti content exceeds 0.10% by mass, a coarse intermetallic compound such as TiAl 3 may crystallize during ingot casting, which may reduce press formability and bending workability in the final plate. It is not preferable.
- the Ti content is in the range of 0.005 to 0.10% by mass.
- a more preferable Ti content is in the range of 0.005 to 0.07 mass%.
- a more preferable Ti content is in the range of 0.01 to 0.05% by mass.
- Mg Less than 0.10% by mass Mg causes a relatively thick oxide film to be formed on the surface of the final plate (annealed plate). As a result, the final plate needs to be sufficiently pickled, resulting in a cost increase. Become. Furthermore, since the Si content is relatively high within the range of the alloy composition of the present invention, when Mg is contained, Mg 2 Si is crystallized, so that elongation is lowered and formability is lowered. Therefore, the preferable Mg content is in the range of less than 0.10% by mass. A more preferable Mg content is in the range of less than 0.05% by mass. A more preferable Mg content is in the range of less than 0.03% by mass.
- Cu Less than 0.8% by mass Cu is an element that increases the strength of the aluminum alloy plate, and is an arbitrary element. In the present invention, if the Cu content is in the range of less than 0.8% by mass, characteristics such as bending workability and shape freezing property do not deteriorate. However, when the Cu content is 0.8% by mass or more, the corrosion resistance is remarkably lowered. Therefore, the preferable Cu content is set to a range of less than 0.8% by mass. A more preferable Cu content is in a range of less than 0.5% by mass. Furthermore, preferable Cu content is the range of less than 0.2 mass%.
- the 3000 series aluminum alloy sheet not only has high strength and excellent formability when applied to automobile body sheets and the like.
- the strength of the material can be known from the tensile strength at the time of the tensile test, the moldability can be known from the elongation value at the tensile test, and the shape freezing property can be known from the yield strength at the tensile test.
- the final annealed plate has a tensile strength of 155 MPa or more and a 0.2% proof stress of 100 MPa or less. Those having a characteristic of elongation of 26% or more are preferred.
- the area ratio of second phase particles having an equivalent circle diameter of 1 ⁇ m or more is 1.5 to 3.5%
- the average crystal grain size is 20 to 50 ⁇ m
- a texture may be used.
- the average crystal grain size in the recrystallized texture to 20 to 50 ⁇ m, it is possible to prevent rough skin after press molding or bending, and a press molded product having an excellent surface appearance can be obtained.
- the area ratio of ⁇ 100 ⁇ -oriented crystals parallel to the plate surface in the recrystallized texture and the ⁇ 123 ⁇ ⁇ 634> orientation parallel to the plate surface The ratio of AR ⁇ 100 ⁇ / AR ⁇ 123 ⁇ ⁇ 634>, which is a ratio with the area ratio of the crystal, needs to be 4.8 or more.
- the area ratio of second phase particles having an equivalent circle diameter of 1 ⁇ m or more is used as the final annealed plate.
- a material having a recrystallization texture of 1.5 to 3.5%, an average crystal grain size of 20 to 50 ⁇ m, and AR ⁇ 100 ⁇ / AR ⁇ 123 ⁇ ⁇ 634> of 4.8 or more is preferable.
- the raw material is charged into the melting / melting melting furnace and the predetermined melting temperature is reached, the flux is appropriately charged and stirred, and further, if necessary, degassing in the furnace using a lance or the like, Hold the sedation to separate the soot from the surface of the melt.
- the molten aluminum alloy melted in the melting furnace may be cast after it is once transferred to the holding furnace, but may be cast directly from the melting furnace.
- a more desirable sedation time is 45 minutes or more.
- in-line degassing is mainly of a type in which an inert gas or the like is blown into a molten aluminum from a rotating rotor, and hydrogen gas in the molten metal is diffused and removed in bubbles of the inert gas.
- nitrogen gas is used as the inert gas, it is important to control the dew point to, for example, ⁇ 60 ° C. or lower.
- the amount of hydrogen gas in the ingot is preferably reduced to 0.20 cc / 100 g or less.
- the reduction rate per pass in the cold rolling process is regulated to, for example, 20% or more to reduce the porosity. It is preferable to crush.
- the hydrogen gas that is supersaturated in the ingot is deposited at the time of spot welding, for example, even after press forming of the final plate, depending on the heat treatment conditions such as annealing of the cold roll. In some cases, a large number of blow holes are generated. For this reason, the more preferable amount of hydrogen gas in the ingot is 0.15 cc / 100 g or less.
- Thin slab continuous casting machine includes both twin belt casting machine and twin roll casting machine.
- the twin belt casting machine includes an endless belt and a pair of rotating belt portions facing each other up and down, a cavity formed between the pair of rotating belt portions, and a cooling means provided inside the rotating belt portion.
- the molten metal is supplied into the cavity through a nozzle made of a refractory, and a thin slab is continuously cast.
- the twin roll casting machine includes a pair of rotating roll portions that are provided with endless rolls so as to face each other, a cavity formed between the pair of rotating roll portions, and a cooling unit provided inside the rotating roll portion.
- the molten metal is supplied into the cavity through a nozzle made of a refractory, and a thin slab is continuously cast.
- the thin slab continuous casting machine can continuously cast a thin slab having a thickness of 2 to 15 mm. If the slab thickness is less than 2 mm, even if casting is possible, it will be difficult to achieve a final rolling rate of 70 to 95%, which will be described later, depending on the thickness of the final plate. When the slab thickness exceeds 15 mm, it is difficult to wind the slab directly on a roll. In this slab thickness range, the cooling rate of the slab is about 40 to 1000 ° C./sec in the vicinity of the slab thickness 1 ⁇ 4, and the intermetallic compound such as Al— (Fe ⁇ Mn) —Si is fine. Crystallized out.
- intermetallic compounds second phase particles having an equivalent circle diameter of 1 ⁇ m or more is 1.5 to 3.5% in the final annealed plate.
- These fine intermetallic compounds serve as nuclei of recrystallized grains during the final annealing of the cold-rolled sheet described later, and the average crystal grain size of the recrystallized grains in the final sheet can be adjusted to 20 to 50 ⁇ m.
- a slab is continuously cast using a cold rolling thin slab continuous casting machine, and the slab is directly wound on a roll without hot rolling, and then cold rolled. For this reason, the chamfering process, the homogenization process, and the hot rolling process required for the conventional semi-continuous cast DC slab can be omitted.
- the roll directly wound with the thin slab is passed through a cold rolling machine and usually subjected to several passes of cold rolling. At this time, since work hardening occurs due to plastic strain introduced by cold rolling, an intermediate annealing treatment may be performed in a batch furnace at a holding temperature of 300 to 400 ° C. for 1 to 8 hours as necessary.
- Final cold rolling rate 70-95% After cold rolling with a final cold rolling rate of 70 to 95%, final annealing is performed. If the final cold rolling rate is within this range, the average grain size in the final plate after annealing can be set to 20-50 ⁇ m, the elongation value can be 26% or more, and the appearance skin after press molding is beautiful. Can be finished. Therefore, it is possible to obtain recrystallized grains adjusted to 20 to 50 ⁇ m in the final annealing process by keeping the processing cost low and adding the processing while securing the solid solution amount of the transition metal element to accumulate the dislocations. It becomes.
- the final cold rolling rate is less than 70%, the amount of work strain accumulated during cold rolling is too small, and 20-50 ⁇ m recrystallized grains cannot be obtained by final annealing.
- the final cold rolling rate exceeds 95%, the amount of processing strain accumulated during cold rolling is too large, the work hardening is severe, the edge cracks at the edges, and rolling becomes difficult. Therefore, a preferable final cold rolling rate is in the range of 70 to 95%. A more preferable final cold rolling rate is in the range of 75 to 95%. A more preferable final cold rolling rate is in the range of 75 to 90%.
- the final annealing that is held for 10 to 60 seconds at a holding temperature of 450 to 560 ° C. by a continuous annealing furnace is preferably a continuous annealing treatment that is held for 10 to 60 seconds at a holding temperature of 450 to 560 ° C. by a continuous annealing furnace. If it cools rapidly after that, it can also serve as a solution treatment. In order to improve the press formability and bending workability in the mold forming process, it is necessary to prepare a solution treatment material.
- Mn dissolved in the matrix by the final annealing is absorbed by the finely crystallized intermetallic compound, thereby promoting recrystallization and reducing the yield strength of the final annealing plate and increasing the elongation.
- the density of ⁇ 123 ⁇ ⁇ 634> orientation crystals parallel to the plate surface in the metal structure decreases, and the density of ⁇ 100 ⁇ orientation crystals parallel to the plate surface increases.
- the holding temperature When the holding temperature is less than 450 ° C., it is difficult to obtain a recrystallized structure. If the holding temperature exceeds 560 ° C., thermal strain becomes severe and burning may occur depending on the alloy composition. If the holding time is less than 10 seconds, the actual temperature of the coil does not reach a predetermined temperature, and the annealing process may be insufficient. If the holding time exceeds 60 seconds, the process takes too much time and productivity is lowered.
- final annealing is an essential step.
- the average crystal grain size is 20 to 50 ⁇ m and further parallel to the plate surface.
- the ratio of AR ⁇ 100 ⁇ / AR ⁇ 123 ⁇ ⁇ 634> which is the ratio of the area ratio of the ⁇ 100 ⁇ orientation crystal and the area ratio of the ⁇ 123 ⁇ ⁇ 634> orientation crystal parallel to the plate surface, is 4.8 or more.
- a recrystallized texture can be developed.
- the Taylor factor in bending is statistically reduced in all directions within the plate surface, so that the slip in the ⁇ 111 ⁇ plane within the crystal grain is relatively small. Deformation becomes easy, and it is considered that bending workability is excellent. Moreover, since the average crystal grain size is adjusted to 20 to 50 ⁇ m, the mean free path of movable dislocations within the crystal grains is sufficient for local plastic processing such as bending. It is thought that it is getting bigger. By passing through the normal continuous casting process as described above, an aluminum alloy plate excellent in bending workability and shape freezing property can be obtained.
- the crucible was taken out from the small electric furnace, and the molten metal was poured into a water-cooled mold having an inner size of 200 ⁇ 200 ⁇ 16 mm to produce a thin slab.
- the disk samples of the respective test materials (Examples 1 to 5 and Comparative Examples 1 to 6) collected from the molten metal in the crucible were subjected to composition analysis by emission spectroscopic analysis. The results are shown in Table 1. After chamfering both sides of this thin slab by 3 mm to obtain a thickness of 10 mm, cold rolling was performed without applying homogenization treatment and hot rolling to obtain a cold rolled material having a plate thickness of 1.0 mm. . In addition, the intermediate annealing process is not performed during the cold rolling process. The final cold rolling rate in this case was 90%.
- Table 1 shows the component composition of the final plate (test material) thus obtained as a thin slab continuous casting simulation material.
- the final annealed plate (each sample material) obtained was subjected to crystal orientation measurement by EBSD.
- a longitudinal section parallel to the rolling direction was cut out from each of the obtained specimens and subjected to mirror polishing, and further subjected to electrolytic polishing to remove distortion caused by polishing.
- the crystal orientation was measured by EBSD.
- the scanning electron microscope used was JSM 6490A manufactured by JEOL Ltd., and was set under the conditions of an acceleration voltage of 15 kV, a WD of 3 mm, and an inclination of 65 °.
- the EBSD measurement was carried out using an OIM type manufactured by TSL Solutions, Inc., and an area of 0.16 to 0.32 square millimeters was measured in 2 ⁇ m steps.
- the obtained results were analyzed by analysis software (OIM analysis), and the area ratio of ⁇ 100 ⁇ orientation crystal parallel to the plate surface and the area ratio of ⁇ 123 ⁇ ⁇ 634> orientation crystal parallel to the plate surface were determined.
- the ⁇ 100 ⁇ azimuth is an azimuth in the range of ⁇ 100 ⁇ to 10 °.
- the ⁇ 123 ⁇ ⁇ 634> azimuth (S azimuth) is an azimuth within a range of 15 ° from ⁇ 123 ⁇ ⁇ 634>.
- the average crystal grain size (equivalent circle diameter) was calculated by analysis software. The measurement results are shown in Table 2.
- a test material having a tensile strength of 155 MPa or more was considered to have good strength, and a test material having a tensile strength of less than 155 MPa was considered to be insufficient in strength.
- a specimen having a 0.2% proof stress of 100 MPa or less was considered good shape freezing property, and a specimen material exceeding 100 MPa was regarded as poor shape freezing property.
- the test material having an elongation value of 26% or more was regarded as having good moldability, and the test material having an elongation value of less than 26% was regarded as having poor moldability.
- the evaluation results are shown in Table 3.
- test pieces for the bending test As test pieces for the bending test, test pieces having a size of 25 mm x 50 mm were taken with respect to each test material with the 90 ° direction as the longitudinal direction with respect to the rolling direction. The bending test was performed by compressing the test pieces until they were in close contact with each other after bending from 40 ° to 60 ° in a state where the direction of 90 ° with respect to the longitudinal direction of the test pieces was pressed against a punch having a punch diameter of 1 mm. The evaluation of bending workability was performed by ranking from 0 to 5 points from no cracks / wrinkles to fractures according to the surface condition of the bent part after contact bending. The test material that was 0 to 1 point was evaluated as having good bending workability, and the test material that was 2 to 5 was rated as poor bending workability.
- Comparative Example 1 is outside the composition range of the present invention, the average crystal grain size is 14 ⁇ m, does not satisfy the standard value, and the ratio of AR ⁇ 100 ⁇ / AR ⁇ 123 ⁇ ⁇ 634> is 4.6. The standard value was not met.
- Comparative Example 2 is outside the composition range of the present invention, the average crystal grain size is 14 ⁇ m, does not meet the standard value, and the ratio AR ⁇ 100 ⁇ / AR ⁇ 123 ⁇ ⁇ 634> is 4.6. The standard value was not met.
- Comparative Example 3 was outside the composition range of the present invention, the average crystal grain size was 16 ⁇ m, and did not satisfy the standard value.
- Comparative Example 4 is outside the composition range of the present invention, the average crystal grain size is 18 ⁇ m, does not satisfy the standard value, and the ratio of AR ⁇ 100 ⁇ / AR ⁇ 123 ⁇ ⁇ 634> is 2.8. The standard value was not met.
- Comparative Example 5 is outside the composition range of the present invention, the area ratio of the second phase particles is 4.4%, does not satisfy the standard value, the average crystal grain size is 17 ⁇ m, and satisfies the standard value The ratio of AR ⁇ 100 ⁇ / AR ⁇ 123 ⁇ ⁇ 634> was 2.7, which did not satisfy the standard value.
- Comparative Example 6 was outside the composition range of the present invention, the area ratio of the second phase particles was 4.7%, did not satisfy the standard value, and was an unrecrystallized structure, The direction is not measured.
- Comparative Example 1 had a high Mg content of 0.35% by mass, the alloy composition was outside the scope of the present invention, and the formability evaluation was poor (x).
- Comparative Example 2 had a high Mg content of 0.34% by mass, the alloy composition was outside the scope of the present invention, and had poor formability evaluation (x) and poor bending workability evaluation (x).
- the Mg content is as high as 0.25% by mass
- the Fe content is as high as 0.61% by mass
- the alloy composition is outside the scope of the present invention, and the formability evaluation is poor (x), bending The workability evaluation was poor (x).
- the Mg content is as high as 0.26% by mass
- the alloy composition is outside the scope of the present invention, and the shape freezeability evaluation failure (x), the formability evaluation failure (x), and the bending workability evaluation failure. (X).
- Comparative Example 5 the Si content was as low as 0.49% by mass, the Fe content was as high as 1.00% by mass, the alloy composition was outside the scope of the present invention, and the strength was insufficient (x).
- the Si content is as high as 1.08% by mass
- the Mn content is as high as 1.98% by mass
- the Zn content is as high as 1.19% by mass
- the alloy composition is out of the scope of the present invention.
- the final annealed plate has a tensile strength of 155 MPa or more, a 0.2% proof stress of 100 MPa or less, and an elongation of 26 It can be seen that it exhibits a value of at least% and is excellent in bending workability.
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Abstract
Description
これによると、熱間圧延の圧延方向に対する冷間圧延の圧延方向を90°となるように設定することで、等二軸変形、平面ひずみ変形、及び一軸変形での破断限界を高めて、プレス成形に適したプレス成形用アルミニウム合金板を提供することができるとのことである。
これによると、鋳塊に150℃以上でしかも非再結晶温度域内の温度で、50%を越える圧下率で粗圧延を行ない、さらに150℃以上でしかも非再結晶温度域内の温度で、ロール周速比1.2~4.0の異周速圧延を、50%を越える圧下率で行なって最終板厚とし、その後溶体化処理を行なうことにより、上記したような再結晶集合組織が得られるとのことである。
これによると、電磁撹拌しながらDC鋳造することで、35%以上の伸び、0.85以上の平均r値、33mm以上の球頭張出高さ、および2.17以上の限界絞り比の全てを達成できるとのことである。
強度を高めるために、さらに、Cu:0.8質量%未満を含有するものであってもよい。
前記最終焼鈍として、保持温度450~560℃で10~60秒保持する連続焼鈍を施すことが望ましい。
したがって、本発明により、自動車用ボディーパネル等に適用可能な成形性および形状凍結性に優れた高強度アルミニウム合金板が廉価で提供される。
したがって、用いる材料として、高強度で、伸びが高く、耐力が低く、且つ再結晶集合組織を適切に制御したものが求められる。
本発明者等は、再結晶集合組織の調査を通じて、成形性、特に曲げ加工性と形状凍結性に優れたアルミニウム合金板を得るべく鋭意検討を重ね、本発明に到達した。
以下にその内容を説明する。
Mnは、アルミニウム合金板の強度を増加させる元素であり、一部はマトリックス中に固溶して固溶体強化を促進するため、必須元素である。また、Mnは、本発明の合金組成の範囲内では、鋳造時にAl-(Fe・Mn)-Si等の微細な金属間化合物を構成する元素でもあり、さらに最終焼鈍時には、マトリックスに固溶していたMnも、一部微細な金属間化合物として析出し、強度を高くする。
Feは、鋳塊鋳造時の冷却速度にもよるが、Al-(Fe・Mn)-Si等の微細な金属間化合物を晶出させ、アルミニウム合金板の強度を増加させる。また、最終焼鈍時には、マトリックスに固溶するMnの一部がこれら金属間化合物に拡散吸収されるので、最終焼鈍板の耐力を低下させるとともに伸びを高める。これら微細な金属間化合物が最終焼鈍時において再結晶粒の核として作用して、再結晶の結晶粒径を所定の範囲に調整することにより、プレス成形後の肌荒れを防止することができるので、必須の元素である。
Siは、鋳塊鋳造時の冷却速度にもよるが、Al-(Fe・Mn)-Si等の微細な金属間化合物を晶出させ、アルミニウム合金板の強度を増加させる。また、一部はマトリックス内に固溶し、強度を高める。最終焼鈍時には、マトリックスに固溶するMnの一部がこれら金属間化合物に拡散吸収されるので、最終焼鈍板の耐力を低下させるとともに伸びを高める。これら微細な金属間化合物が最終焼鈍時において再結晶粒の核として作用して、再結晶の結晶粒径を所定の範囲に調整することにより、プレス成形後の肌荒れを防止することができるので、必須の元素である。
Tiは鋳塊鋳造時に結晶粒微細化剤として作用し、鋳造割れを防止することができるので、必須の元素である。勿論、Tiは単独で添加してもよいが、Bと共存することによりさらに強力な結晶粒の微細化効果を期待できるので、Al-5%Ti-1%Bなどのロッドハードナーでの添加であってもよい。
Mgは、最終板(焼鈍板)の表面に比較的厚い酸化皮膜を生成させる原因となり、その結果、最終板を十分に酸洗いする必要が生じコストアップの要因となる。さらに本発明の合金組成の範囲内では、Si含有量が比較的高いため、Mgを含有すると、Mg2Siが晶析出するため、伸びが低くなり成形性を低下させる。したがって、好ましいMgの含有量は、0.10質量%未満の範囲とする。より好ましいMg含有量は、0.05質量%未満の範囲である。さらに好ましいMg含有量は、0.03質量%未満の範囲である。
Cuは、アルミニウム合金板の強度を増加させる元素であり、任意の元素である。本発明において、Cu含有量は、0.8質量%未満の範囲であれば、曲げ加工性および形状凍結性等の特性について低下することはない。しかしながら、Cu含有量が0.8質量%以上であると、耐食性が著しく低下する。したがって、好ましいCuの含有量は、0.8質量%未満の範囲とする。より好ましいCu含有量は、0.5質量%未満の範囲である。さらに好ましいCu含有量は、0.2質量%未満の範囲である。
不可避的不純物は原料地金、返り材等から不可避的に混入するもので、それらの許容できる含有量は、例えば、Crの0.20質量%未満、Znの0.20質量%未満、Niの0.10質量%未満、Ga及びVの0.05質量%未満、Pb、Bi、Sn、Na、Ca、Srについては、それぞれ0.02質量%未満、その他各0.05質量%未満であって、この範囲で管理外元素を含有しても本発明の効果を妨げるものではない。
ところで、3000系アルミニウム合金板を自動車用ボディーシート等に適用するに当たっては、高強度と優れた成形性を有するだけでなく、プレス成形時の形状凍結性にも優れることが必要である。
材料の強度は引張り試験を行った時の引張強度で、成形性は引張り試験時の伸びの値で、また形状凍結性は引張り試験時の耐力によって知ることができる。
平均結晶粒径:20~50μm
AR {100} /AR {123}<634> 比:4.8以上
上記のような特性は、前記特定の成分組成を有する3000系アルミニウム合金板の金属組織を細かく調整することにより発現される。
具体的には、金属組織は、円相当径1μm以上の第二相粒子の面積率が1.5~3.5%であり、平均結晶粒径を20~50μm、板面に平行な{100}方位結晶の面積率と板面に平行な{123}<634>方位結晶の面積率との比であるAR{100}/AR{123}<634>比を4.8以上である再結晶集合組織にすればよい。特に、再結晶集合組織における平均結晶粒径を20~50μmにすることにより、プレス成形後や曲げ加工後の肌荒れを防止することができ、表面外観の優れたプレス成型品を得ることができる。また、曲げ加工における微小割れなどの不良発生率を低減するためには、再結晶集合組織における板面に平行な{100}方位結晶の面積率と板面に平行な{123}<634>方位結晶の面積率との比であるAR{100}/AR{123}<634>比を4.8以上とする必要がある。
溶解・溶製
溶解炉に原料を投入し、所定の溶解温度に到達したら、フラックスを適宜投入して攪拌を行い、さらに必要に応じてランス等を使用して炉内脱ガスを行った後、鎮静保持して溶湯の表面から滓を分離する。
インライン脱ガスは、回転ローターからアルミニウム溶湯中に不活性ガス等を吹き込み、溶湯中の水素ガスを不活性ガスの泡中に拡散させ除去するタイプのものが主流である。不活性ガスとして窒素ガスを使用する場合には、露点を例えば-60℃以下に管理することが重要である。鋳塊の水素ガス量は、0.20cc/100g以下に低減することが好ましい。
薄スラブ連続鋳造機は、双ベルト鋳造機、双ロール鋳造機の双方を含むものとする。
双ベルト鋳造機は、エンドレスベルトを備え上下に対峙する一対の回転ベルト部と、当該一対の回転ベルト部の間に形成されるキャビティーと、前記回転ベルト部の内部に設けられた冷却手段とを備え、耐火物からなるノズルを通して前記キャビティー内に金属溶湯が供給されて連続的に薄スラブを鋳造するものである。
薄スラブ連続鋳造機は、厚み2~15mmの薄スラブを連続的に鋳造することが可能である。スラブ厚み2mm未満の場合には、鋳造が可能な場合であっても、最終板の板厚にもよるが、後述する最終圧延率70~95%を実現することが困難となる。スラブ厚み15mmを超えると、スラブを直接ロールに巻き取ることが困難となる。このスラブ厚みの範囲であると、スラブの冷却速度は、スラブ厚さ1/4の付近で、40~1000℃/sec程度となり、Al-(Fe・Mn)-Si等の金属間化合物が微細に晶出する。このため、最終焼鈍板において円相当径1μm以上の金属間化合物(第二相粒子)の面積率が1.5~3.5%である金属組織を発現することが可能となる。これらの微細な金属間化合物は、後述する冷延板の最終焼鈍時に再結晶粒の核となり、最終板における再結晶粒の平均結晶粒径を20~50μmに調整することが可能となる。
薄スラブ連続鋳造機を用いて、スラブを連続的に鋳造し、前記スラブに熱間圧延を施すことなく直接ロールに巻き取った後、冷間圧延を施す。このため、従来の半連続鋳造DCスラブに必要となる面削工程、均質化処理工程、熱間圧延工程を省略することができる。薄スラブを直接巻き取ったロールは、冷延機に通され、通常何パスかの冷間圧延が施される。この際、冷間圧延によって導入される塑性歪により加工硬化が起こるため、必要に応じて、バッチ炉内で保持温度300~400℃で1~8時間保持する中間焼鈍処理を行なってもよい。
最終冷延率70~95%の冷間圧延を施した後、最終焼鈍を施す。最終冷延率がこの範囲であれば、焼鈍後の最終板における平均結晶粒径を20~50μmにして、伸びの値を26%以上にすることができ、プレス成形後の外観肌を綺麗に仕上げることができる。したがって、加工コストを低く抑えるとともに、遷移金属元素の固溶量を確保しながら加工を加えることで転位が蓄積されて、最終焼鈍工程で20~50μmに調整された再結晶粒を得ることが可能となる。最終冷延率が70%未満であると、冷間圧延時に蓄積される加工歪量が少なすぎて、最終焼鈍によって20~50μmの再結晶粒を得ることができない。最終冷延率が95%を超えると、冷間圧延時に蓄積される加工歪量が多すぎて、加工硬化が激しく、エッジに耳割れを生じて圧延が困難となる。したがって、好ましい最終冷延率は、70~95%の範囲である。より好ましい最終冷延率は、75~95%の範囲である。さらに好ましい最終冷延率は、75~90%の範囲である。
連続焼鈍炉により、保持温度450~560℃で10~60秒保持
最終焼鈍は、連続焼鈍炉によって450℃~560℃の保持温度で10~60秒間保持する連続焼鈍処理が好ましい。その後急速に冷却すれば、溶体化処理を兼ねることもできる。金型成形工程におけるプレス成形性や曲げ加工性を高めるためには、溶体化処理材としておくことが必要である。最終焼鈍によって、マトリックスに固溶していたMnは、微細に晶出していた金属間化合物に吸収されることにより、再結晶が促進されるとともに、最終焼鈍板の耐力を低下させ、伸びを高める。同時に、金属組織における板面に平行な{123}<634>方位結晶の存在密度が減少し、板面に平行な{100}方位結晶の存在密度が増加する。
以上のような通常の連続鋳造工程を経ることにより、曲げ加工性および形状凍結性に優れたアルミニウム合金板を得ることができる。
表1に示した11水準の組成(合金No.1~11)に配合された各種インゴット各5kgを#20坩堝内に挿入し、この坩堝を小型電気炉で加熱しインゴットを溶解した。次いで、溶湯中にランスを挿入して、N2ガスを流量1.0L/minで5分間吹き込んで脱ガス処理を行なった。その後30分間の鎮静を行なって溶湯表面に浮上した滓を攪拌棒にて除去した。次に坩堝を小型電気炉から取り出して、溶湯を内寸法200×200×16mmの水冷金型に流し込み、薄スラブを作製した。坩堝中の溶湯から採取した各供試材(実施例1~5、比較例1~6)のディスクサンプルは、発光分光分析によって組成分析を行なった。その結果を表1に示す。この薄スラブの両面を3mmずつ面削加工して、厚さ10mmとした後、均質化処理、熱間圧延を施すことなく、冷間圧延を施して板厚1.0mmの冷延材とした。なお、冷間圧延工程の間に中間焼鈍処理は行っていない。この場合の最終冷延率は90%であった。
得られた最終焼鈍板(各供試材)について、EBSDによる結晶方位測定を行った。得られた各供試材から圧延方向に平行な縦断面を切出して鏡面研磨を施し、さらに研磨によるひずみを除去するために電解研磨を施した。この試験片について、EBSDによる結晶方位の測定を行った。走査電子顕微鏡は日本電子製JSM6490Aを用い、加速電圧15kV、WD3mm、65°の傾斜の条件に設定した。EBSD測定は(株)TSLソリューションズ製OIM型により、0.16から0.32平方ミリメートルの領域を2μmステップで測定した。得られた結果を、解析ソフト(OIM analysis) によって解析し、板面に平行な{100}方位結晶の面積率と板面に平行な{123}<634>方位結晶の面積率を求めた。ここで、{100}方位は{100}から10°の範囲にある方位とした。{123}<634>方位(S方位)は{123}<634>から15°の範囲にある方位とした。同様に、解析ソフトによって平均結晶粒径(円相当径)を算出した。測定結果を、表2に示す。
得られた最終板の圧延方向に平行な縦断面(LT方向に垂直な断面)を切り出して、熱可塑性樹脂に埋め込んで鏡面研磨し、フッ化水素酸水溶液にてエッチングを施して、金属組織観察を行った。ミクロ金属組織を光学顕微鏡にて写真撮影し(1視野当たりの面積;0.017mm2、各試料20視野撮影)、写真の画像解析を行い、円相当径1μm以上の第2相粒子の面積率を求めた。測定結果を、表2に示す。
得られた最終板(各供試材)の特性評価は、引張り試験の引張強度、0.2%耐力、伸び(%)によって行った。
具体的には、得られた供試材より、引張り方向が圧延方向に対して平行方向になるようにJIS5号試験片を採取し、JISZ2241に準じて引張り試験を行って、引張強度、0.2%耐力、伸び(破断伸び)を求めた。なお、これら引張り試験は、各供試材につき3回(n=3)行い、その平均値で算出した。
最終板において、引張強度が155MPa以上であった供試材を強度良好とし、155MPa未満であった供試材を強度不足とした。また0.2%耐力が100MPa以下であった供試材を形状凍結性良好とし、100MPaを超えた供試材を形状凍結性不良とした。さらに伸びの値が26%以上であった供試材を成形性良好とし、26%未満であった供試材を成形性不良とした。評価結果を表3に示す。
曲げ試験用の試験片として、各供試材について圧延方向に対して90°方向を長手方向として25mm×50mm寸法の試験片を採取した。曲げ試験は、試験片の長手方向に対して90°方向をポンチ径1mmのポンチに押し当てた状態で、40°から60°に曲げたあと、試験片同士が密着するまで圧縮加工した。曲げ加工性の評価は、密着曲げ後の曲げ部の表面状態によって、割れ・シワなし~破断までを0~5点の点数でランク付けすることにより行った。0~1点であった供試材を曲げ加工性評価良好とし、2~5点であった供試材を曲げ加工性評価不良とした。
各供試材の金属組織評価結果を示す表2における実施例1~5は、本発明の組成範囲内であり、AR{100}/AR{123}<634>比、平均結晶粒径、第二相粒子の面積率とも、基準値を満たしていた。すなわち、具体的には、AR{100}/AR{123}<634>比:4.8以上、平均結晶粒径:20~50μm、円相当径1μm以上の第二相粒子の面積率:1.5~3.5%の要件を満たしていた。
供試材の特性評価結果を示す表3における実施例1~5は、本発明の組成範囲内であり、引張強度、0.2%耐力、伸び、曲げ加工性とも全て、基準値を満たしていた。具体的には、引張強度:155MPa以上、0.2%耐力:100MPa以下、伸び:26%以上、曲げ加工性:0~1点の基準値を満たしていた。なお、比較例1,5,6については、曲げ試験を行っていないため、曲げ加工性については不明である。
Claims (4)
- Mn:1.0~1.6質量%、Fe:0.1~0.8質量%、Si:0.5~1.0質量%、Ti:0.005~0.10質量%を含有し、不純物としてのMgを0.10質量%未満に規制し、残部がAlおよび不可避的不純物からなる成分組成を有し、金属組織は、円相当径1μm以上の第二相粒子の面積率が1.5~3.5%であり、平均結晶粒径が20~50μm、板面に平行な{100}方位結晶の面積率と板面に平行な{123}<634>方位結晶の面積率との比であるAR{100}/AR{123}<634>比が4.8以上である再結晶集合組織を呈するとともに、引張強度155MPa以上、0.2%耐力100MPa以下、伸び26%以上であることを特徴とする曲げ加工性と形状凍結性に優れた高強度アルミニウム合金板。
- さらに、Cu:0.8質量%未満含有することを特徴とする請求項1に記載の曲げ加工性と形状凍結性に優れた高強度アルミニウム合金板。
- 請求項1または請求項2に記載の組成のアルミニウム合金溶湯を薄スラブ連続鋳造機を用いて、厚み2~15mmのスラブを連続的に鋳造し、前記スラブに熱間圧延を施すことなく直接ロールに巻き取った後、冷間圧延を施し、最終冷延率70~95%の冷間圧延を施した後、最終焼鈍を施すことを特徴とする曲げ加工性と形状凍結性に優れた高強度アルミニウム合金板の製造方法。
- 連続焼鈍炉により、保持温度450~560℃で10~60秒保持する最終焼鈍を施す請求項3に記載の曲げ加工性と形状凍結性に優れた高強度アルミニウム合金板の製造方法。
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CN111141772A (zh) * | 2019-09-17 | 2020-05-12 | 闽南理工学院 | 一种纯铝系合金ebsd试样的制备方法 |
JP7319450B1 (ja) * | 2022-12-19 | 2023-08-01 | Maアルミニウム株式会社 | アルミニウム合金圧延材 |
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