JP4312819B2 - Aluminum alloy sheet with excellent ridging marks during molding - Google Patents

Description

  The present invention relates to an aluminum alloy plate excellent in ridging mark properties (hereinafter, aluminum is also simply referred to as Al), and can suppress surface irregularities (also referred to as ridging marks and roping) that occur during press forming of a panel. -It relates to a Si-based aluminum alloy plate. The aluminum alloy plate referred to in the present invention refers to a plate that has been subjected to tempering such as solution treatment and quenching after rolling and before being formed into a panel by press molding or the like.

  In recent years, with respect to global environmental problems caused by exhaust gas and the like, improvement in fuel efficiency has been pursued by reducing the weight of the body of a transport aircraft such as an automobile. For this reason, in particular, the application of lighter aluminum alloy materials excellent in formability and bake hardenability is increasing in place of steel materials that have been used in the past for automobile bodies.

  Among these, panels such as outer panels (outer plates) and inner panels (inner plates) of panel structures such as automobile hoods, fenders, doors, roofs, and trunk lids are thin and high-strength aluminum alloy plates. The use of Al-Mg-Si-based AA to JIS 6000-based (hereinafter also simply referred to as 6000-based) aluminum alloy plates has been studied.

  The 6000 series aluminum alloy sheet basically contains Si and Mg as essential, and has excellent age-hardening ability. Therefore, in press forming and bending processing, formability is ensured by reducing the yield strength and forming. BH properties (bake hardness, artificial age hardening ability) that can ensure the required strength by age hardening by heating at the time of processing, such as paint baking treatment of the subsequent panel, and heat resistance during treatment. Paint bake hardenability).

  Further, the 6000 series aluminum alloy plate has a relatively small amount of alloy elements as compared with other 5000 series aluminum alloys having a large amount of alloy such as Mg. For this reason, when the scraps of these 6000 series aluminum alloy sheets are reused as the aluminum alloy melting material (melting raw material), the original 6000 series aluminum alloy ingot is easily obtained, and the recyclability is excellent.

  On the other hand, as is well known, an outer panel of an automobile is manufactured by combining an aluminum alloy plate with a forming process such as an extension forming in a press forming or a bending forming. For example, a large outer panel such as a hood or a door is formed into a molded product shape as an outer panel by press forming such as overhanging, and then the inner panel and the inner panel are formed by hem (hemming) processing such as flat hem at the outer peripheral edge of the outer panel. Are joined to form a panel structure.

  At this time, the panel after press molding using a 6000 series aluminum alloy plate as a raw material has a problem that surface rough defects such as ridging marks are likely to occur. The ridging mark is a phenomenon resulting from unevenness on the surface of the plate at the time of deformation such as press molding due to the texture arranged in the shape of stripes on the plate. For this reason, even if the crystal grains of the aluminum alloy plate as a raw material are fine enough not to cause rough skin, the point caused by press molding is troublesome.

  This ridging mark is particularly likely to occur when the press molding conditions become severe due to an increase in the size, complexity, or thickness of the panel structure. In addition, there is a problem that it becomes relatively inconspicuous immediately after press molding and becomes conspicuous after proceeding to the coating process as it is as a panel structure.

  When this ridging mark is generated, a panel structure for an outer plate (outer) or the like, which is required to have a particularly beautiful surface, has a problem in appearance and cannot be used.

  Conventionally, the ingot is cooled after homogenization heat treatment at a temperature of 500 ° C. or higher, or reheated after cooling to room temperature, and heated at a relatively low temperature of 350 to 450 ° C. It is known to prevent ridging marks on excess Si type 6000 series aluminum alloy plates by starting rolling or controlling the compound (see Patent Documents 1, 2, 3, and 10).

  Various methods for improving the ridging mark by controlling the texture (crystal orientation) of the 6000 series aluminum alloy plate have been proposed. For example, focusing on the crystal orientation component of the {100} plane, it has been proposed to refine the degree of Cube orientation accumulation in the plate surface layer portion to 2 to 5 and the crystal grain size of the plate surface portion to 45 μm or less ( (See Patent Document 4). In addition, it has been proposed to simultaneously define the distribution density of various orientations such as Cube orientation, Goss orientation, Brass orientation, CR orientation, RW orientation, S orientation, and PP orientation in a 6000 series aluminum alloy plate ( (See Patent Documents 5 and 9).

Furthermore, it has also been proposed that the proportion of crystal grain boundaries whose adjacent crystal orientation difference is 15 ° or less is 20% or more (see Patent Document 6). It has also been proposed that the ear rate in a 6000 series aluminum alloy plate is 4% or more and the crystal grain size is 45 μm or less (see Patent Document 7). In addition, an aluminum alloy containing Mg, the area ratio of the crystal grains whose crystal plane orientation on the alloy surface is within 10 ° from the (100) plane, and the crystal grains within 20 ° from the (100) plane It has also been proposed to make the area ratio occupied by a specific relationship (see Patent Document 8).
Japanese Patent No. 2823797 JP-A-8-232052 JP-A-7-228956 JP-A-11-189836 JP-A-11-236639 JP 2003-171726 A Japanese Unexamined Patent Publication No. 2000-96175 JP 2005-146310 A JP 2004-292899 A JP 2005-240113 A

  The prior art has a certain effect in suppressing ridging marks, including controlling the texture and characteristics of the plates as in Patent Documents 4 to 9. However, when the molding conditions become more severe, such as molding into a deeper or more complicated three-dimensional panel, the effect is still insufficient.

  The present invention has been made by paying attention to such circumstances, and its purpose is to prevent ridging marks during press molding with high reproducibility, which becomes prominent when the molding conditions become more severe. An object of the present invention is to provide an Al—Mg—Si based aluminum alloy plate.

  In order to achieve this object, the gist of the aluminum alloy plate excellent in ridging mark property at the time of forming of the present invention is mass%, Mg: 0.1-3.0%, Si: 0.1-2. 5%, Mn: 0.01 to 1.0%, Cu: 0.001 to 1.0%, the balance being an Al—Mg—Si based aluminum alloy plate made of Al and inevitable impurities. Average texture of Goss orientation area ratios in the cross-section of each plate when the width between the plate widths is divided every 250 μm. The value is 3% or less, and the difference between the maximum value and the minimum value of each area ratio in the Goss orientation is 2% or less. The average value is 10% or less, and these And the difference between the maximum value and the minimum value among the area ratio of the ube orientation is 5% or less.

  Here, the aluminum alloy plate is Fe: 1.0% or less, Cr: 0.3% or less, Zr: 0.3% or less, V: 0.3% or less, Ti: 0.1% or less, Ag : Allowed to contain one or more of 0.2% or less, Zn: 1.0% or less.

  The present inventors examined whether the ridging mark of an aluminum alloy plate, which had been visually evaluated until now, could be quantified and evaluated. In this study, the panel (panel) that was actually formed into a deeper or more complex three-dimensional panel with ridging marks on the surface was compared with the panel that did not occur (panel). The surface roughness of these plates (panels) was measured with a tracer (three-dimensional shape measuring instrument). Then, the obtained three-dimensional shape data on the surface of the plate (panel) was subjected to frequency analysis using analysis software.

  As a result, the ridging marks (surface irregularities) generated on the plate (panel) are relatively large with a length in the plate width direction of about 2 to 3 mm. It was found that it has a period. In other words, in the present invention, it is quantitatively clarified that the ridging mark whose occurrence is remarkable has a relatively large period of about 2 to 3 mm in the plate width direction. First successful.

  On the other hand, in the texture control technology of the plate in the conventional patent document described above, when analyzing and evaluating the ridging mark, it can be evaluated only in a narrow region (length) having a plate width of about 3 mm at the maximum. Absent. For example, in patent document 9, in the Example, in the area | region of 3 mm of board widths, the texture in each board cross section when this board width is each divided | segmented every 500 micrometers is measured. However, this means that the ridging mark having the large period can be evaluated only for one period at most. That is, in the texture control technology of the plate in the above-described conventional patent document, when the press molding conditions become more severe, the occurrence becomes remarkable, and the length in the plate width direction is about 2 to 3 mm. A ridging mark having a large period cannot be taken into account, including variations in surface irregularities.

  And this, coupled with the fact that the evaluation of the ridging marks was limited to visual qualitative evaluation, was one factor that the effect of suppressing the ridging marks was still insufficient even by the texture control of the conventional plate. It is assumed that

  In the present invention as well, the mechanism of ridging mark generation, in which the introduction strain amount (crystalline deformation amount) of adjacent crystal grains differs depending on the crystal orientation of the plate, and ridging marks that are uneven surface irregularities are likely to occur. In addition, the perception of this mechanism is the same as in the above-mentioned patent document that defines the crystal orientation.

  However, in the present invention, in consideration of the period of the ridging marks and the magnitude of variation, the length of 20 mm, which is a relatively wide area of the Al-Mg-Si based aluminum alloy plate, which is longer than the period of the ridging marks. First of all, the point of improving the formability by defining the state of the texture between the plate widths is greatly different. In the present invention, in particular, the Goss direction and the Cube direction in such a relatively wide area in the plate width direction are selected as control targets. That is, in addition to restricting each of these orientations in the relatively wide region in the plate width direction by each average area ratio and minimizing them as much as possible, the Goss orientation existing in the relatively wide region in the plate width direction Each deviation from the Cube orientation is defined by the difference between the maximum value and the minimum value of each area ratio, and is reduced as much as possible.

  This prevents the generation of ridging marks having a relatively large period when the molding conditions become more severe, such as being molded into a deeper or more complex three-dimensional panel. An Al—Mg—Si based aluminum alloy plate that can be produced can be provided.

  Hereinafter, embodiments of the aluminum alloy plate of the present invention will be specifically described.

(Gathering organization)
The Goss orientation and the Cube orientation have very large in-plane anisotropy of r value (Rankford value) compared to other orientations. In the Goss orientation, the thickness decreases when the plate is pulled in the width direction. Hardly occurs. When the Goss orientation having such characteristics is present in the structure in a substantial amount, when the plate is press-molded, the elongation deformation ability differs depending on the portion of the plate, particularly the portion in the width direction of the plate, and extends in the width direction of the plate. Elongation deformation capacity is reduced. On the other hand, the Cube orientation is the main orientation of the recrystallized texture of aluminum, as is generally known, and is one of the main crystal orientations in Al-Mg-Si alloys. In the Cube orientation, unlike the Goss orientation, the plate thickness is remarkably reduced when the plate is pulled in the 45 ° direction with respect to the rolling direction.

  When a substantial amount of Goss orientation and Cube orientation in which the thickness reduction behavior is completely different (similarly or both) exist in the structure at the same time, naturally, when the plate is press-molded, naturally, the portion of the plate, especially the plate In the width direction, the unevenness on the surface of the plate varies greatly.

  According to the recognition of the present inventors, the distribution state of the Goss orientation and the Cube orientation in the relatively wide area in the plate width direction described above is a ridging mark (plate) when the molding conditions become more severe. This is the main cause of the occurrence of large irregularities on the surface. For this reason, in the present invention, in order to suppress this ridging mark, not only the respective orientations of the Goss orientation and the Cube orientation in the relatively wide area of the above-described plate are restricted, but also the relatively wide area. The deviation of each of these directions is also minimized.

  Specifically, in an Al—Mg—Si-based aluminum alloy plate, this is a textured state between the plate widths over an arbitrary 20 mm length of the plate, and the interval between the plate widths is every 250 μm. The average value of the area ratios of the Goss orientations at the section of each of the sections at the time of division is 3% or less, and the difference between the maximum value and the minimum value of the area ratios of these Goss orientations Is not more than 2%, and the average value of each area ratio of the Cube orientation is 10% or less, and the maximum value and the minimum value of each area ratio of the Cube orientation are not more than 10%. And the difference is 5% or less.

  As described above, the ridging marks (surface irregularities) generated on the Al—Mg—Si based aluminum alloy plate have a relatively large period in which the length in the plate width direction is about 2 to 3 mm. For this reason, in consideration of the variation, the average value of the area ratios of the Goss direction and the Cube direction in each plate section in the plate width direction in a comparatively large (wide) measurement range over a length of 20 mm or more at the minimum. Must be suppressed to 3% or less and 10% or less.

  In addition, the difference between the maximum value and the minimum value of the area ratios of the Goss orientations in the cross sections of each section (80 places) when the board width of 20 mm is divided every 250 μm. Is 2% or less, and it is necessary that the difference between the maximum value and the minimum value of the area ratios of the Cube orientation is 5% or less.

  This reduces the Goss orientation and the Cube orientation in the texture that causes ridging marks and the texture that causes ridging marks in the width direction of the Al—Mg—Si-based aluminum alloy plate. The fluctuation of the is also sufficiently small. As a result, the main factor of ridging marks has been eliminated, and even when the molding conditions for deeper or more complex three-dimensional panels such as overhang molding of large automobile panels such as hoods and doors have become more severe. The surface quality of the plate is greatly improved.

  Next, FIG. 1 is used to support the correlation between the ridging mark, the Goss orientation in the texture, and the Cube orientation. Fig. 1 shows the results of measuring the shape of a ridging mark on the surface of the plate (the surface of the plate on which the ridging mark was generated) in the plate width direction with a tracer (three-dimensional shape measuring instrument), and the structure in the plate width direction measured by EBSP. (Plate cross section), changes in the area ratios of the Goss orientation and the Cube orientation (plate cross section) are also shown.

  In FIG. 1, the vertical direction of the figure is the plate thickness direction, the upper side of the figure is the surface side of the plate (measurement surface side), and the horizontal direction of the figure is the plate width direction. The measurement length in the plate width direction is 6 mm. The measurement plate of FIG. 1 is a comparative example 9 in an example (Table 3) described later.

  It is to be noted that the present invention is the first time that the ridging mark itself has been grasped and ridging mark property evaluation has been quantitatively performed by measuring and analyzing the plate surface unevenness profile with the above-described tracer. The quantitative grasp of the ridging mark itself is also significant because the quantitative grasp of the ridging mark itself is the basis of the present invention. Further, this quantitative grasp leads to a quantitative scale for evaluating the ridging mark property based on the amplitude (μm) of the peaks and valleys of the concavo-convex curve in the plate surface concavo-convex profile as in Examples described later. The tracer measurement conditions and analysis method for quantitatively grasping the ridging mark itself will be described in detail in Examples described later.

  In FIG. 1, the uppermost figure shows the structure measured by EBSP. In FIG. 1, the second diagram from the top shows changes in the plate width direction (plate cross section) of the respective area ratios of Goss orientation and Cube orientation. In this figure, the second broken line (thick line) from the top is the Cube orientation, and the third broken line (bottom line) from the top (thick line) is the Goss orientation. In this figure, the change in the plate width direction of the total area ratio of the Brass orientation, the S orientation, and the Cu orientation is also indicated by the top broken line (thin line) for reference. Further, in FIG. 1, lower ones 1 to 3 indicate changes in the plate width direction of ridging marks (unevenness on the plate surface) generated on the plate, the shape of which was measured by the above-described tracer.

  FIG. 2 is a perspective view showing the measurement positions of the respective items of the plate as the measurement target in FIG. The horizontal direction of the plate in FIG. 2 is the rolling direction (RD direction, plate longitudinal direction), and the diagonally up and down direction is the plate width direction. Is stretched 20% in the direction perpendicular to The plate surface portions 1 to 3 whose shapes are measured by the tracer of FIG. 1 correspond to the three portions 1 to 3 which are oriented in the plate width direction of FIG. 2 and spaced by 1 mm from each other in the rolling direction. Moreover, in FIG. 2, the EBSP measurement surface of the board cross section on the right side of the board (cross section extending in the board width direction) is indicated by an arrow.

  In the broken line showing the change in the area ratio between the Goss orientation and the Cube orientation in FIG. 1, the concave portion where the area ratio on the vertical axis (the level of the broken line) is the lowest is the minimum value of each area ratio. On the other hand, the convex part where the area ratio (the level of the broken line) on the vertical axis is the highest is the maximum value of each area ratio.

  On the other hand, in the curve (broken line) indicating the change in the plate width direction of the ridging marks 1 to 3 (unevenness on the plate surface) on the lower side of FIG. The lowest concave part is a part where the plate surface is concave and the plate thickness is smaller than the original plate thickness (plate thickness before stretching). Moreover, the convex part where the height of the unevenness on the vertical axis (curve level) is the highest is the part where the plate surface is convex and the plate thickness is close to the original plate thickness (plate thickness before stretching). .

  Based on the above, when analyzing the texture of FIG. 1 (Comparative Example 9 in Example Table 3) in which ridging marks are generated on the plate, first, the Goss orientation and the Cube orientation have developed too much, and the average area The rate exceeds the upper limit of the present invention and each is too large. In FIG. 1, the average area ratio of Goss orientation is 6.0%, and the average area ratio of Cube orientation is 12.4%. In addition, in the texture of FIG. 1, the change in the sheet width direction of each area ratio between the Goss orientation and the Cube orientation is relatively large. In the Goss orientation, the difference between the maximum value and the minimum value of the area ratio in the plate width direction is 3.5%, and in the Cube orientation, the difference between the maximum value and the minimum value of the area ratio in the plate width direction is 6.0%. Each exceeding the upper limit of the present invention is too large.

  On the other hand, when the ridging mark of FIG. 1 is analyzed, first, the change in the plate width direction of the unevenness of the plate surface in each of the above-described points 1 to 3 is relatively large, and the length of the unevenness of the ridging mark in the plate width direction is first. It can be seen that the thickness (change) has a relatively large period of about 2 to 3 mm. It can be seen that the area ratios of the Goss orientation and the Cube orientation also change in the plate width direction in accordance with the length (change) of the unevenness in the plate width direction of the ridging mark.

  This is in contrast to the fact that the change in the plate width direction of the total area ratio of the Brass, S, and Cu orientations shown in FIG. 1 is relatively small. In other words, crystal orientations other than the Goss orientation and the Cube orientation, such as the Brass orientation, the S orientation, and the Cu orientation, do not significantly affect the generation of ridging marks having a relatively large period of about 2 to 3 mm. I understand that. Therefore, it is not necessary to regulate crystal orientations other than Goss orientation and Cube orientation, and a substantial amount may exist in the measurement region in the plate width direction of Goss orientation and Cube orientation.

  That is, it can be confirmed from FIG. 1 that the distribution state of the Goss orientation and the Cube orientation in a relatively wide area of the plate is the main factor for the occurrence of unevenness (riding marks) on the plate surface as described above. It is done. Further, in order to suppress the ridging mark, as described above, not only the Goss orientation and the Cube orientation in the relatively wide area of the plate are restricted, but also the Goss existing in the relatively wide area. It is supported that the deviation between the azimuth and the Cube azimuth (difference between the maximum value and the minimum value of the area ratio in the plate width direction) should be reduced as much as possible.

  In the present invention, the value of the plate width length of 20 mm, which is the texture measurement range, and the value of the interval of 250 μm separating the plate widths are the length (change) of the unevenness in the plate width direction of the ridging marks. It is defined as the minimum necessary measurement condition that can correspond to a relatively large period of about 2 to 3 mm and can reliably suppress ridging marks. In other words, even if the plate width to be measured is increased or the interval between the plate widths is narrowed, the range in which the measured values do not differ greatly or the range in which the measured values are reproducible is selected. .

(Measurement of texture of aluminum alloy sheet)
The formation of the texture differs depending on the processing method even if the crystal system is the same. That is, as shown below, the rolling surface is represented by {xxx} and the rolling direction is represented by <ΔΔΔ>. In addition, (circle) and (triangle | delta) have shown the integer.

Based on such an expression method, each direction is expressed as follows. The expression of each orientation is described in “Cross texture” written by Shinichi Nagashima (published by Maruzen Co., Ltd.) and “Light metal” commentary Vol.43 (1993) P.285-293.
Cube orientation: {001} <100>
Goss orientation: {011} <100>
CR orientation: {001} <520>
RW orientation: {001} <110> [Cube orientation in which (100) plane rotates the plate surface]
Brass orientation: {011} <211>
S orientation: {123} <634>
Cu orientation: {112} <111>
(Or D orientation: {4411} <11118>)
SB orientation: {681} <112>

(Measurement of crystal orientation component abundance)
For the area ratio (existence ratio) of each crystal orientation component of these crystal grains, a backscattered electron diffraction image EBSP (Electron Backscatter Diffraction Pattern) obtained by scanning electron microscope SEM (Scanning Electron Microscope) was used for the above-described plate cross section. Measured by crystal orientation analysis method (SEM / EBSP method).

  In the crystal orientation analysis method using the EBSP, the surface of the sample set in the SEM column is irradiated with an electron beam to project the EBSP on the screen. This is taken with a high-sensitivity camera and captured as an image on a computer. In the computer, the orientation of the crystal is determined by analyzing this image and comparing it with a pattern obtained by simulation using a known crystal system.

  The crystal orientation analysis method using the EBSP is not a measurement for each crystal grain, but is performed by scanning a specified sample region at an arbitrary fixed interval, and the above process is automatically performed for all measurement points. Therefore, tens of thousands to hundreds of thousands of crystal orientation data are obtained at the end of measurement. For this reason, there is an advantage that the observation field is wide and the average crystal grain size, the standard deviation of the average crystal grain size, or the information of the orientation analysis can be obtained within a few hours for a large number of crystal grains. Therefore, it is optimal when the above-mentioned wide-area texture in the plate width direction is specified or measured as in the present invention.

  On the other hand, in X-ray diffraction (X-ray diffraction intensity, etc.) generally used for texture measurement, a relatively micro area for each crystal grain as compared with the crystal orientation analysis method using EBSP. This means that the organization (texture) is measured. For this reason, the wide-area structure (texture structure) in the plate width direction that affects the ridging mark cannot be measured as accurately and efficiently as the crystal orientation analysis method using the EBSP.

  In the crystal orientation analysis method using the EBSP, a specimen for observing a structure is taken from each cross section of the plate, subjected to mechanical polishing and buffing, and then subjected to electrolytic polishing to adjust the surface. For the test piece thus obtained, for example, an SEM (JEOLJSM5410) manufactured by JEOL Ltd., for example, an EBSP measurement / analysis system manufactured by TSL: OIM (Orientation Imaging Macrograph, analysis software name “OIMA Analysis”) is used as the SEM device. Then, it is determined whether each crystal grain has a target orientation (within 10 ° from the ideal orientation), and the orientation density in the measurement visual field is obtained. The measurement area of the test piece is 1000 μm × 1000 μm, and the measurement step interval is, for example, 3 μm or less.

  At this time, the measurement area of the material to be measured is usually divided into hexagonal areas, and a Kikuchi pattern is obtained from the reflected electrons of the electron beam incident on the sample surface for each of the divided areas. At this time, if the electron beam is scanned two-dimensionally on the sample surface and the crystal orientation is measured at every predetermined pitch, the orientation distribution on the sample surface can be measured. Next, the obtained Kikuchi pattern is analyzed to know the crystal orientation at the electron beam incident position. That is, the obtained Kikuchi pattern is compared with data of a known crystal structure, and the crystal orientation at the measurement point is obtained. Similarly, the crystal orientation of the measurement point adjacent to the measurement point is obtained, and those whose crystal orientation difference is within ± 15 ° (deviation within ± 15 ° from the crystal plane) are located on the same crystal plane. Shall belong. Further, when the orientation difference between both crystals exceeds ± 15 °, the interval (such as the side where both hexagons are in contact) is defined as the grain boundary. In this way, the distribution of grain boundaries on the sample surface is obtained. The measurement visual field range is, for example, an area of about 500 μm × 500 μm, and this is measured at an appropriate number of places on the test piece and averaged.

(Average crystal grain size)
In order to suppress the ridging mark, it is preferable to reduce the average crystal grain size, in other words, not to increase the crystal grain size. That is, it is preferable that each average crystal grain size in the plate cross section is 50 μm or less. Further, by making the crystal grain size fine or small in this range, bending workability and press formability are ensured or improved. When the crystal grain size becomes larger than 50 μm, even if the crystal orientation is controlled, the press formability such as bending workability and overhang is remarkably deteriorated, and defects such as cracking and roughening occur during molding. easy.

  Here, the average crystal grain size is obtained by measuring the maximum diameter in the rolling direction of each crystal grain plate observed in a predetermined measurement region using the SEM-EBSP and measurement conditions thereof. The average value is calculated.

(Chemical composition)
The chemical component composition of the 6000 series aluminum alloy plate targeted by the present invention will be described. The 6000 series aluminum alloy plate targeted by the present invention is required to have excellent properties such as formability, BH property, strength, weldability, and corrosion resistance as a plate for an automobile outer plate.

  In order to satisfy such requirements, the composition of the aluminum alloy plate is, in mass%, Mg: 0.1-3.0%, Si: 0.1-2.5%, Mn: 0.01-1 0.0%, Cu: 0.001 to 1.0%, with the balance consisting of Al and inevitable impurities. In addition,% display of content of each element means the mass% altogether.

  The 6000 series aluminum alloy plate targeted by the present invention tends to generate ridging marks, but has an excellent BH property, and has an Si-Mg mass ratio of Si / Mg of 1 or more. It is preferably applied to an aluminum alloy plate. The 6000 series aluminum alloy sheet secures formability by reducing the yield strength during press molding and bending, and is age-hardened by heating during relatively low temperature artificial aging treatment such as paint baking treatment of the panel after molding. Yield strength is improved, and it has excellent age-hardening ability (BH property) that can secure the required strength. Among these, the excess Si type 6000 series aluminum alloy plate is more excellent in this BH property than the 6000 series aluminum alloy plate having a mass ratio Si / Mg of less than 1.

  Other elements other than Mg, Si, Mn, and Cu are basically impurities, and the content (allowable amount) of each impurity level in accordance with AA or JIS standards. However, from the viewpoint of recycling, not only high-purity Al bullion but also 6000 series alloys and other aluminum alloy scrap materials, low-purity Al bullion, etc. Other elements may be mixed as impurities. Then, reducing these impurity elements to, for example, below the detection limit itself increases the cost, and a certain amount of allowance is required. Moreover, even if it contains a substantial amount, there is a content range that does not hinder the object and effect of the present invention, and within this range, there is also a content effect of each element.

  Therefore, these impurity elements are allowed to be contained within the ranges specified below. Specifically, Fe: 1.0% or less, Cr: 0.3% or less, Zr: 0.3% or less, V: 0.3% or less, Ti: 0.1% or less, Ag: 0.2 % Or less and Zn: 1.0% or less may be further included within this range in addition to the basic composition described above. Here, it is assumed that all upper limit regulations for these elements do not include 0%.

  The preferable content range and significance of each element in the 6000 series aluminum alloy, or the allowable amount will be described below.

Si: 0.1-2.5%
Si, together with Mg, forms an aging precipitate that contributes to strength improvement during solid tempering and artificial aging treatment at low temperatures such as paint baking treatment, and exhibits age hardening ability, which is necessary as an outer panel for automobiles. For example, it is an essential element for obtaining the required strength (proof strength) of 180 MPa or more. Therefore, in the excess Si type 6000 series aluminum alloy plate of the present invention, it is the most important element for combining various properties of bending workability such as press formability and hemming.

  In addition, in order to demonstrate the excellent low-temperature age-hardening ability of 180 MPa or more after the low-temperature paint baking treatment after molding on the panel (at the time of low-temperature aging treatment at 170 ° C. × 20 minutes after applying 2% stretch) It is preferable to have an excess Si type 6000 series aluminum alloy composition in which Si / Mg is 1.0 or more by mass and Si is excessively contained with respect to Mg.

  If the Si content is less than 0.1%, the age-hardening ability and further various properties such as press formability and bending workability required for each application cannot be obtained. Furthermore, recrystallization is promoted by soaking and hot rolling, and the Goss orientation and the Cube orientation are easily developed, and the Goss orientation and the Cube orientation cannot be suppressed and controlled within the scope of the present invention. On the other hand, when Si exceeds 2.5%, press formability including bending workability and ridging mark property is remarkably inhibited. In addition, weldability is significantly impaired. Therefore, Si is in the range of 0.1 to 2.5%, preferably in the range of 0.6 to 1.2%.

Mg: 0.1-3.0%
Mg forms an aging precipitate that contributes to strength improvement together with Si during the above-mentioned artificial aging treatment such as solid solution strengthening and paint baking treatment, and exhibits age-hardening ability. As a panel, for example, a required proof stress of 180 MPa or more It is an essential element for obtaining.

  If the Mg content is less than 0.1%, the absolute amount is insufficient, so that the compound phase cannot be formed during the artificial aging treatment, and the age hardening ability cannot be exhibited. For this reason, the required proof stress of 180 MPa or more necessary for the panel cannot be obtained. Furthermore, recrystallization is promoted by soaking and hot rolling, and the Goss orientation and the Cube orientation are easily developed, and the Goss orientation and the Cube orientation cannot be suppressed and controlled within the scope of the present invention.

  On the other hand, when Mg exceeds 3.0%, the formability such as press formability and bending workability including ridging mark property is significantly inhibited. Therefore, the Mg content is in the range of 0.1 to 3.0%, preferably such that Si / Mg is 1.0 or more by mass ratio. When the Si content is in the range of 0.6 to 1.2%, the Mg content is preferably in the range of 0.2 to 0.7%.

Cu: 0.001 to 1.0%
Cu has the effect of accelerating the formation of aging precipitates that contribute to the improvement of strength in the crystal grains of the aluminum alloy material structure under the conditions of artificial aging treatment at a relatively low temperature and short time of the present invention. Moreover, solid solution Cu also has the effect of improving moldability. This effect is not obtained when the Cu content is less than 0.001%, particularly less than 0.01%. On the other hand, if it exceeds 1.0%, the stress corrosion cracking resistance, the thread rust resistance of the corrosion resistance after coating, and the weldability are remarkably deteriorated. Therefore, the Cu content is set to 0.001 to 1.0%, preferably 0.01 to 1.0%.

Mn: 0.01 to 1.0%
Mn produces dispersed particles (dispersed phase) during the homogenization heat treatment, and these dispersed particles have the effect of preventing grain boundary movement after recrystallization, so that there is an effect that fine crystal grains can be obtained. . As described above, the press formability and hemmability of the aluminum alloy sheet of the present invention improve as the crystal grains of the aluminum alloy structure become finer. In this respect, when the Mn content is less than 0.01%, these effects are not obtained.

  On the other hand, when the Mn content increases, coarse Al-Fe-Si- (Mn, Cr, Zr) -based intermetallic compounds and crystal precipitates are easily generated during melting and casting, and the mechanical properties of the aluminum alloy sheet are increased. Causes the properties to deteriorate. Further, when the Mn content exceeds 1.0%, the bending workability is lowered. For this reason, Mn is in the range of 0.01 to 1.0%, preferably in the range of 0.01 to 0.15%.

(Production method)
Next, a method for producing the aluminum alloy plate of the present invention will be described below. The aluminum alloy sheet of the present invention is a conventional process or a known process, and the aluminum alloy ingot having the above-mentioned 6000 series component composition is subjected to homogenization heat treatment after casting, and then subjected to hot rolling and cold rolling to obtain a predetermined process. It is manufactured by being subjected to a tempering treatment such as solution hardening and quenching. However, among these, in order to improve the ridging mark property, in order to control the texture of the Goss orientation and the Cube orientation within the scope of the present invention, the cooling rate conditions and soaking conditions described below are controlled. There is a need.

(Melting, casting)
First, in the melting and casting process, an ordinary molten casting method such as a continuous casting method or a semi-continuous casting method (DC casting method) is appropriately selected for the molten aluminum alloy adjusted to be dissolved within the above-mentioned 6000 series component composition range. Cast.

(Casting cooling rate)
However, the cooling rate during casting is large (fast) from the melting temperature (about 700 ° C.) to the liquidus temperature of 150 ° C./min or more and from the liquidus temperature to the solidus temperature of 100 ° C./min or more. It is preferable to do. However, the temperature (cooling rate) control in the high temperature region from the melting temperature (about 700 ° C.) to the liquidus temperature has been conventionally performed regardless of whether it is continuous casting or DC casting. Is hardly done. In such a case, the cooling rate in this high temperature region is inevitably slow.

  Thus, when the cooling rate in the high temperature region becomes slow, the amount of crystallized material generated coarsely in the temperature range in this high temperature region increases, and the size of the crystallized material in the plate width direction of the ingot And the variation of the quantity becomes large. Such a tendency is that the cooling rate from the dissolution temperature (about 700 ° C.) to the liquidus temperature is less than 150 ° C./min, and the cooling rate from the liquidus temperature to the solidus temperature is less than 100 ° C./min. In this case, it becomes particularly remarkable.

  This causes a large variation in the crystal orientation in the ingot, and the Goss orientation and the Cube orientation are easily developed, and the Goss orientation and the Cube orientation are suppressed and controlled within the scope of the present invention in order to improve the ridging mark property. Can not do. In addition, if the cooling rate in each of these high temperature regions is small, the amount of Mg and Si dissolved in the ingot decreases, so that the subsequent soaking and recrystallization in hot rolling are promoted, the Goss orientation and The Cube orientation is easily developed, and the Goss orientation and the Cube orientation cannot be suppressed and controlled within the scope of the present invention.

(Homogenization heat treatment)
Next, the cast aluminum alloy ingot is subjected to a homogenization heat treatment. As the homogenization heat treatment temperature itself, a homogenization temperature of 500 ° C. or higher and lower than the melting point is appropriately selected as usual. The purpose of this homogenization heat treatment (soaking) is to homogenize the structure, that is, eliminate segregation in crystal grains in the ingot structure. When this homogenization temperature is low, segregation within the crystal grains cannot be sufficiently eliminated, and this acts as a starting point of fracture, so that stretch flangeability and bending workability are deteriorated.

  However, the heating temperature rising condition during the soaking process is 200 ° C. or lower and kept at a low temperature of 100 ° C. or higher for 2 to 10 hours (h), and then at a rate of 300 ° C./hour (h) or higher 500 ° C. or higher. Heat to homogenization temperature. By maintaining at a low temperature of 200 ° C. or lower and 100 ° C. or higher in the initial stage of soaking, fine precipitates can be uniformly dispersed. This fine precipitate significantly suppresses the growth of Goss orientation and Cube orientation. In this so-called first-stage soaking process at a low temperature, if the holding temperature exceeds 200 ° C. or the holding time exceeds 10 hours, the precipitates become coarse, and such an effect is lost. The direction becomes easy to develop. Further, if this holding temperature is less than 2 hours, the holding time is insufficient.

  Subsequently, soaking is performed at a temperature of 500 ° C. or higher to sufficiently dissolve the alloy elements and coarse compounds, but the heating rate from the above holding temperature to 500 ° C. or higher is lower than 300 ° C./hour (slow). In the meantime, the Mg—Si compound or simple substance Si is coarsely precipitated and remains until after the soaking. Thereby, the solid solution amount of the alloy element and the coarse compound is also reduced, and recrystallization after the hot rolling process is promoted, so that the Goss orientation and the Cube orientation are easily developed. Therefore, it is preferable that the heating and heating rate from the above holding temperature to the soaking temperature is higher (faster) than 300 ° C./hour.

  Further, it is preferable that the cooling rate after soaking is large (fast). When the ingot (slab) becomes larger or the ingot is cooled in a batch soaking furnace, the cooling rate after the homogenization heat treatment is less than about 20 ° C./hr. When the ingot (slab) is large, the cooling rate is about 30 to 40 ° C./hr even if it is left outside the batch soaking furnace. When cooling with such a normal cooling means, the cooling rate is insufficient, precipitates such as Mg-Si compounds are coarsened, and Goss orientation and Cube orientation are likely to develop. Therefore, it is preferable to cool the ingot after the homogenization heat treatment using a forced cooling means such as a fan so that the cooling rate is 40 ° C./hr or more.

(Hot rolling)
Hot rolling is a rough rolling process for ingots (slabs) according to the sheet thickness to be rolled, and a finish rolling process for rolling a sheet having a thickness of about 40 mm or less after rough rolling to a thickness of about 4 mm or less. Consists of In these rough rolling process and finish rolling process, a reverse type or a tandem type rolling mill is used as appropriate, and rolling consisting of a plurality of passes is performed.

  Here, in order to prevent the Goss orientation and the Cube orientation from developing in the texture of the plate, the following specific hot rolling conditions are preferable. That is, it is preferable that the start temperature in the rough rolling is in a temperature range of 400 to 550 ° C., the total processing rate in the finish rolling is 90% or more, and the finish rolling finish temperature is 400 ° C. or less.

  For example, when the hot rolling (rough rolling) start temperature is less than 400 ° C., recrystallization does not proceed after the hot rolling is completed, and the processed structure remains, so that ridging marks are easily generated. On the other hand, when the hot rough rolling start temperature exceeds 550 ° C., recrystallization occurs, coarse recrystallized grains are generated during hot rolling, and Goss orientation and Cube orientation are easily developed. Become.

  Further, when the end temperature of hot rolling (finish rolling) exceeds 400 ° C., coarse recrystallized grains are generated, and Goss orientation and Cube orientation are easily developed, which causes ridging marks. On the other hand, even if the hot rolling end temperature is less than 300 ° C., recrystallization does not proceed after the end of hot rolling, the processed structure remains, and ridging marks are easily generated. Therefore, the hot rolling end temperature is preferably 300 ° C. or higher and 400 ° C. or lower.

(Hot rolled sheet annealing)
It is preferable not to perform the annealing (roughening) of the hot-rolled sheet before cold rolling basically. By omitting this annealing (roughening), it is possible to improve the efficiency of manufacturing the plate and reduce the manufacturing cost.

(Cold rolling)
In cold rolling, the hot-rolled sheet is rolled to produce a cold-rolled sheet (including a coil) having a desired final thickness.

(Solution and quenching)
In order to suppress ridging marks in the final solution treatment and quenching process, the Goss orientation and the Cube orientation are suppressed by utilizing dispersed particles controlled within the scope of the present invention by soaking of the ingot. In order to achieve this, it is preferable that the temperature increase rate of the final solution treatment is 100 ° C./min or more.

  The solution treatment conditions are preferably 500 ° C. or more, preferably a melting point in order to sufficiently precipitate aging precipitates that contribute to strength improvement by artificial aging treatment such as paint baking hardening after press molding of the plate. Perform in the following temperature range.

In the quenching treatment from the solution treatment temperature, if the cooling rate is slow, Si, Mg ₂ Si, etc. are likely to precipitate on the grain boundary, which is likely to become the starting point of cracks during press molding and bending, and these formability decreases. To do. In order to ensure this cooling rate, the quenching treatment may be performed by selecting and using water cooling means and conditions such as air cooling of a fan, mist, spray, immersion, etc., respectively, and rapid cooling at a cooling rate of 10 ° C./second or more. preferable.

  In the present invention, in order to further enhance the age-hardening property in the artificial age-hardening treatment such as the paint baking process of the molded panel, a pre-aging treatment is performed after the quenching treatment in order to promote the precipitation of the age-related precipitates that contribute to strength improvement. You may do it. This preliminary aging treatment is preferably held in a temperature range of 60 to 150 ° C., preferably 70 to 120 ° C. for a required time of 1 to 24 hours. As the preliminary aging treatment, the cooling end temperature of the quenching treatment is increased to 60 to 150 ° C., and then immediately reheated or held as it is. Alternatively, after the solution treatment, after the quenching treatment to room temperature, it is immediately reheated to 60 to 150 ° C. within 5 minutes.

  Furthermore, in order to suppress aging at room temperature, heat treatment (artificial aging treatment) at a relatively low temperature may be performed after the preliminary aging treatment without time delay. When the time delay is present, room temperature aging (natural aging) occurs with time even after the preliminary aging treatment, and after the room temperature aging occurs, the effect of the heat treatment at the relatively low temperature is exhibited. It becomes difficult.

  Further, in the case of continuous solution quenching, the quenching process is completed within the temperature range of the preliminary aging, and the coil is wound around a coil at the same high temperature. In addition, you may reheat before winding up to a coil, and you may heat-retain after winding. Moreover, after the quenching process to room temperature, it may be reheated to the above temperature range and wound at a high temperature.

  In addition to this, it is of course possible to further increase the strength by performing aging treatment or stabilization treatment at a higher temperature according to the application or required characteristics.

  EXAMPLES Hereinafter, the present invention will be described more specifically with reference to examples. However, the present invention is not limited by the following examples, but may be appropriately modified within a range that can meet the purpose described above and below. It is also possible to implement, and they are all included in the technical scope of the present invention.

  Next, examples of the present invention will be described. A 6000 series aluminum alloy plate having the composition of A to K shown in Table 1 is subjected to homogenization heat treatment (abbreviated as soaking) and hot rolling (abbreviated as hot rolling) under the conditions shown in Table 2, and further cold rolled. Was manufactured by solution treatment and quenching. In addition, in the display of the content of each element in Table 1, the display of “−” indicates that it is below the detection limit.

  More specific production conditions for the aluminum alloy plate are as follows. Ingots of 500 mm thickness, 2000 mm width, and 7 m length of each composition shown in Table 1 were commonly melted by DC casting. At this time, as shown in Table 2, the cooling rate during casting (° C./min) is changed from the melting temperature (about 700 ° C.) common to each example to the liquidus temperature (about 650 ° C. which is almost the same in each example). ) And from this liquidus temperature to the solidus temperature (about 590 ° C., which is almost the same in each example).

  In the subsequent soaking process of the ingot, as shown in Table 2, the conditions for holding at a low temperature during heating and heating (the soaking process at the first stage low temperature: ° C x h) and soaking process are performed. The heating temperature rising rate (° C / h) up to the temperature was changed. In addition, the cooling after the soaking process is common to each example, and the ingot is formed by a fan in a soaking furnace so that the specific cooling rate range of 60 ° C./hr, which is the preferable cooling condition described above, Forced air cooling was performed to a temperature of 200 ° C. or lower.

  After this soaking process, in common with each example, it is reheated to the hot rolling start temperature shown in Table 2, hot rolling (rough rolling) is started at this temperature, and hot rolling to 2.5 mm in thickness (finish rolling). did. Table 2 also shows the end temperature of hot rolling (finish rolling) in each example. These hot rolling conditions were carried out under the preferred temperature conditions described above in common with each example. These hot-rolled sheets were commonly used in each example, and were subjected to direct cold rolling at a cold rolling rate of 60% after omitting the roughening, to obtain cold-rolled sheets having a thickness of 1.0 mm.

  The cold-rolled sheet is heated in a continuous heat treatment facility at a rate of temperature increase of about 300 ° C./min in common with each example, and held for 5 seconds when the solution treatment temperature reaches 550 ° C. Solution treatment was performed, and quenching was performed immediately to room temperature by rapid cooling at a cooling rate of 100 ° C./second or more. Further, within 5 minutes after this quenching (immediately), a preliminary aging (reheating) treatment was carried out at a temperature of 100 ° C. for 2 hours. After this preliminary aging treatment, it was gradually cooled at 0.6 ° C./hr to obtain a T4 tempered material.

  A test plate (blank) was cut out from each final product plate after the tempering treatment, and the structure and characteristics of each test plate after room temperature aging (room temperature standing) on the 15th day after the tempering treatment were measured and evaluated. .

(Test plate structure)
The texture of the test plate after room temperature aging for 15 days after the tempering treatment was measured and analyzed using the SEM-EBSP. The test plate was simulated for severe press forming, and the plate cross section in the plate width direction after stretching 20% in the plate width direction (in the direction perpendicular to the rolling) to give pre-strain was used as the EBSP measurement surface. And when this EBSP measurement surface divides between the plate widths over 20 mm of the center part of the plate width every 250 μm in the plate width direction (however, the interval of 1 to 3 in FIG. 2 is 1 mm). It was set as each board cross section of the divided part. That is, the average value of the area ratios of Goss orientation and Cube orientation, and the difference between the maximum value and the minimum value of the area ratios of Goss orientation and Cube orientation in each plate cross section at these separated locations, Analyzed. At the same time as the EBSP measurement, the average crystal grain size of the test plate was also measured. These results are shown in Table 3.

(Test plate characteristics)
Further, as the characteristics of the test plate, ridging mark property, 0.2% yield strength (As yield strength: MPa), and elongation (%) were measured. These results are also shown in Table 3.

(Riding mark)
While measuring the shape of the texture-measurement / analysis part (plate width center part of the plate) of the test plate after 20% stretching with a tracer (three-dimensional shape measuring instrument), the obtained 3 Dimensional shape data was subjected to frequency analysis using analysis software. The result of frequency analysis of this three-dimensional shape data is illustrated in FIG. FIG. 5 (scan examples 1 to 4) is data of comparative example 9: FIG. 1 to be described later. The vertical axis of FIG. 5 is the height of the surface irregularities of the plate, and the horizontal axis is the length in the plate width direction. In addition, the location of the plate surface whose shape was measured with this tracer was the plate surface in the vicinity of the EBSP measurement surface of the test plate (1 of 1 to 3 in FIG. 2).

The shape measurement conditions of the tracer were a measurement probe tip R 25 μm, a measurement pitch 25 μm, and a measurement distance (plate width direction) 6000 μm (6 mm). Then, the surface roughness measurement data of this tracer is analyzed using the analysis software VIVIAN at the spatial frequency (in terms of spatial period in μm), the vertical axis is the frequency, and the horizontal axis is the relationship with the spatial frequency. An uneven profile was created. As a result of analyzing this profile, in each comparative example in which ridging marks are generated, the spatial frequency is about 3 to 5 × 10 ⁻⁴ μm, and when converted to a spatial period, it is prominent at 2 to 3 μm (feature) ) Peak was observed. This surface unevenness profiling data is illustrated in FIG. 6 (scan examples 1 to 4). A portion surrounded by a dotted circle in FIG. 6 is a characteristic peak at 2 to 3 μm in terms of a spatial period. This is the basis that the ridging marks (surface irregularities) generated on the plate have a relatively large period extending in the plate width direction of about 2 to 3 mm.

  Further, this surface unevenness profile was filtered to remove a spatial frequency other than the spatial frequency considered to correspond to the ridging mark as noise, and a correction profile was created. This correction profile is illustrated in FIG. 7 (scan examples 1 to 4). As a result, in the invention example without the ridging mark, the peaks and valleys of the uneven curve in the profile do not correspond to the rolling direction, but in the comparative example with the ridging mark, as shown in FIG. The valley corresponds to the rolling direction. In the profile of the comparative example with the ridging mark, as shown in FIG. 7, the amplitude of the peaks and valleys of the concave and convex curves is significantly larger than that of the invention example without the ridging mark.

  In the present invention, the amplitude (μm) of the peaks and valleys of the concave and convex curve that can be grasped numerically (quantitatively) from among the feature points indicating the presence or absence of ridging marks in the surface concave and convex profile, A measure of ridging mark generation. That is, when the amplitude of the peaks and valleys of the concavo-convex curve was 0.3 μm or less, a ridging mark was not actually generated, and it was evaluated as 優 れ because the press formability was excellent. In addition, when the amplitude exceeded 0.3 μm but was 0.5 μm or less, a ridging mark was generated, but it was relatively mild. Further, when the amplitude exceeded 0.5 μm, a large ridging mark was generated as shown in FIG. 1, and even if the molding conditions were changed, the press formability (ridging mark property) was poor, and the evaluation was x.

  In the tensile test for imparting the stretch, a No. 5 test piece (25 mm × 50 mmGL × plate thickness) of JISZ2201 was collected from an aluminum alloy plate after room temperature aging for 15 days after the tempering treatment, and subjected to room temperature tension. . The tensile direction of the test piece at this time was the direction perpendicular to the rolling direction. The tensile speed was 5 mm / min up to 0.2% proof stress and 20 mm / min after proof stress. The results of measuring 0.2% proof stress and elongation by this method are shown in Table 3 (N number = average value of 5).

  As shown in Tables 1 and 2, each invention example is cast (cooling rate at the time of casting), homogenization heat treatment (low temperature holding, temperature rise / cooling rate) within the composition range of the present invention and in a preferable condition range, and Hot rolling is performed. For this reason, as shown in Table 3, it has a texture defined in the present invention. That is, in order to suppress the ridging mark, not only the Goss orientation and the Cube orientation in the relatively wide area of the above-described plate are restricted, but also the Goss orientation and the Cube existing in the relatively wide area. Each deviation from the bearing is also reduced as much as possible. In each of the inventive examples, the average crystal grain size is also 50 μm or less.

  As a result, each of the inventive examples is an example of a 6000 series aluminum alloy plate having an excess Si type composition that has been aged at room temperature after the tempering treatment and has reduced formability. Excellent markability. It also has excellent mechanical properties such as strength and elongation.

  On the other hand, Comparative Examples 8 to 12 use the same alloy example as that of Invention Example 2. However, as shown in Table 2, in these comparative examples, the production conditions for casting (cooling rate at the time of casting) and homogenization heat treatment (at the time of temperature increase) are out of the preferred ranges. As a result, in these comparative examples, the average amplitude in the unevenness on the plate surface is larger than that of the above-described invention example, and the ridging mark property is inferior.

  In Comparative Example 8, the cooling rate from the melting temperature (about 700 ° C.) to the liquidus temperature and the cooling rate from the liquidus temperature to the solidus temperature are both too low (too slow) in the cooling rate during casting. Comparative Example 9 does not hold a low temperature of 200 ° C. or lower and 100 ° C. or higher among the heating temperature rising conditions during soaking. In Comparative Example 10, this low temperature holding temperature is too low. In Comparative Example 11, the heating temperature increase rate after this low temperature holding is too small (too slow). In Comparative Example 12, this low temperature holding temperature is too high.

  Here, FIG. 3 shows Invention Example 1 and FIG. 4 shows Comparative Example 11 similar to FIG. 1 in the structure in the plate width direction (plate cross section) measured by EBSP, and the area ratios of Goss orientation and Cube orientation. The change in the width direction (plate cross section) is also shown. 3 and 4, the invention example 1 in FIG. 3 has a Goss orientation (bottom thick line at the bottom) in the comparatively wide width direction region of the plate as compared with the comparative example 11 in FIG. ) And the Cube orientation (the thick line at the top of the black circle) is small, and the deviations between the Goss orientation and the Cube orientation existing in this relatively wide width region are also small. I understand. 3 and 4, the thin circled thin line is the Brass orientation, the triangular marked thin line is the S orientation, and the US marked thin line is the Cu orientation. 3 and 4, as in FIG. 1, the vertical direction of the drawing is the plate thickness direction, the upper side of the drawing is the surface side of the plate (measurement surface side), and the horizontal direction of the drawing is the plate width direction. It is.

  Comparative Examples 13 to 16 are in a preferred range, and the component composition is out of the range of the present invention, although casting (cooling rate at the time of casting) and homogenization heat treatment (at the time of raising the temperature) are performed. Accordingly, the ridging mark property is remarkably inferior to that of the inventive example from the viewpoint of the component composition, or the strength and elongation are remarkably inferior to those of the inventive example even if the ridging mark property is good.

  Therefore, the results of the above examples support the critical significance or effect for combining the ridging mark properties, mechanical properties, etc., of the requirements of the components and structures in the present invention, or preferred production conditions.

  According to the present invention, an Al-Mg-Si-based aluminum alloy that can prevent ridging marks during press molding, which are prominent when the molding conditions become more severe, with good reproducibility and excellent mechanical properties. Can provide a board. As a result, the application of the 6000 series aluminum alloy plate can be expanded for transporting devices such as automobiles, ships or vehicles, home appliances, buildings, structural members and parts, and particularly for transporting devices such as automobiles. .

It is explanatory drawing which shows the structure | tissue of an aluminum alloy plate, and the unevenness | corrugation of the surface. It is a perspective view which shows the data collection position in the aluminum alloy plate of FIG. It is explanatory drawing which shows the structure of the board width direction of an example of an invention, and the change (plate cross section) of the board width direction of each area rate of Goss direction and Cube direction. It is explanatory drawing which shows the structure of the board width direction of a comparative example, and the change (plate cross section) of the board width direction of each area ratio of Goss direction and Cube direction. It is explanatory drawing which frequency-analyzed the three-dimensional shape data of the surface of the aluminum alloy plate (comparative example) with the analysis software. It is explanatory drawing which made the surface uneven | corrugated profile the data of FIG. It is explanatory drawing which shows the correction | amendment profile which filtered the surface uneven | corrugated profile of FIG.

Claims (2)

  In mass%, Mg: 0.1-3.0%, Si: 0.1-2.5%, Mn: 0.01-1.0%, Cu: 0.001-1.0%, An Al—Mg—Si-based aluminum alloy plate, the balance of which is made of Al and unavoidable impurities, is a texture between the plate widths over an arbitrary 20 mm length of the plate, and the gap between the plate widths every 250 μm. The average value of the area ratios of the Goss orientations at the section of each of the sections at the time of division is 3% or less, and the difference between the maximum value and the minimum value of the area ratios of these Goss orientations Is not more than 2%, and the average value of the area ratios of the Cube orientation in each plate cross section of the section is 10% or less, and the maximum value and the minimum value of the area ratios of the Cube orientation are Lysine during molding, characterized by a difference of 5% or less Mark excellent in the aluminum alloy plate.   The aluminum alloy plate further comprises Fe: 1.0% or less, Cr: 0.3% or less, Zr: 0.3% or less, V: 0.3% or less, Ti: 0.1% or less, Ag: The ridging mark property at the time of molding according to claim 1, comprising one or more of 0.2% or less, Zn: 1.0% or less (however, these upper limit specifications do not include 0%). Excellent aluminum alloy plate.

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