TWI638897B - Hight surface quality aluminum-magnesium-silicon alloy sheet and method of fabricating the same - Google Patents

Abstract

The present invention is directed to providing a high surface quality aluminum-magnesium-niobium alloy sheet and a method of manufacturing the same. The manufacturing method is to cast a 6000 series aluminum alloy having a main component of 0.8 to 1.5 wt% and 0.25 to 0.7 wt% of magnesium into an aluminum embryo, and then apply the homogenization treatment required for the material, and then pass the designed preheating temperature. The appropriate combination of the rolling reduction rate and the finishing temperature causes the surface grain orientation of the hot rolled sheet to change from directional to scattered, and the state continues until the material is cold rolled into a finished product and finally heat treated. Therefore, after the formed aluminum-magnesium-niobium alloy sheet is formed and painted, the surface thereof is not derived with a rope streak similar to a brush mark.

Description

High surface quality aluminum-magnesium-niobium alloy sheet and its manufacturer law

The present invention provides an aluminum-magnesium-niobium alloy sheet and a method for producing the same, and in particular to a high-surface-quality aluminum alloy sheet having no surface on the surface and a method for producing the same.

Aluminum-magnesium-bismuth alloy has the advantages of light weight, good formability and high strength after baking. After the global energy-saving and carbon-reducing trend, it has gradually replaced steel to make four-door and two-cover. However, after the aluminum-magnesium-niobium alloy sheet is formed, the surface is often derivatized with rope-like stripes, especially after the baking of the paint, so that its application on the outer member is limited.

At present, it is known that the above-mentioned rope-like stripe generation mechanism is mainly due to the fact that the aluminum-magnesium-niobium alloy sheet is subjected to tensile stress in the vertical rolling direction during the manufacturing process, and protrusions and valleys are formed due to uneven deformation. The rough surface, and the above-mentioned protrusions and depressions extend a considerable distance in the rolling direction, so that even after the baking of the paint, it is clearly visible. Figure 1 Shown is an aluminum-magnesium-niobium alloy sheet having a rope-like stripe on the surface after stretching and deformation, wherein the right half of the figure is in the state after the ink is simulated, and the vertical rolling direction is the sandpaper polishing mark. The above-mentioned rope-like stripes are produced on the material due to the special orientation (mainly cubic (Cube{001}<100>) and Gaussian (Goss{011}<100>)). The rolling direction is arranged in a strip shape and is unevenly distributed in the vertical rolling direction.

In view of the defects of the rope-like stripe on the surface of the above-mentioned aluminum-magnesium-niobium alloy sheet, there are two known solutions: (1) increasing the iron content of the aluminum blank during casting, and reducing the rolling ratio during cold rolling to reduce the cube Type and Gaussian grain group formation, which reduces the banding of the rope; and (2) intervening an appropriate intermediate annealing process to promote the particle during the cold rolling of the aluminum-magnesium-bismuth alloy sheet The formation of nucleation (Particle stimulated nucleation (PSN) type crystal grains is caused, so that the distribution of the orientation is dissipated to suppress the generation of cubic crystal grains, thereby reducing the phenomenon of rope streaks.

However, increasing the iron content causes a large amount of coarse cast crystal phase to be formed inside the aluminum-magnesium-niobium alloy sheet, thereby reducing the ductility, and lowering the rolling ratio of the cold rolling causes the aluminum-magnesium-niobium alloy sheet to be crystallized after heat treatment. The granules become coarser, causing the surface of the formed surface to produce rough cellulite, which also affects the appearance. Furthermore, the use of an intermediate annealing process not only consumes additional energy, but also extends the production line and increases production costs.

Therefore, it is urgent to propose an aluminum-magnesium-niobium alloy sheet having a uniformly dispersed and non-directional arrangement of crystal grains on the surface without an intermediate annealing process, and in particular, the surface rope stripes are not obvious. Aluminum-magnesium-niobium alloy sheet.

An aspect of the present invention is to provide a method for producing a high surface quality aluminum-magnesium-niobium alloy sheet, which can obtain a uniformly dispersed and non-directional grain on a surface by an aluminum embryo of a specific composition and a hot rolling step. Type of aluminum-magnesium-niobium alloy sheet.

Another aspect of the present invention is to provide a high surface quality aluminum-magnesium-niobium alloy sheet.

According to the above aspect of the invention, a method for producing a high surface quality aluminum-magnesium-niobium alloy sheet is proposed. In one embodiment, the above manufacturing method comprises the steps of: firstly, providing an aluminum embryo having an alloy composition comprising 0.8% by weight (wt.%) to 1.5% by weight, 0.25 wt.% to 0.7 wt.%. Magnesium, 0.1 wt.% to 0.5 wt.% iron, 0.01 wt.% to 0.2 wt.% manganese, a total amount of less than 0.15 wt.% of one or more impurities, and the balance being aluminum. Next, the aluminum embryo is subjected to a homogenization step. Then, the aluminum blank is further subjected to a hot rolling step to form a hot rolled sheet, wherein the hot rolling step comprises: preheating the aluminum blank, and subjecting the aluminum blank to a hot rolling treatment, wherein the preheating temperature is 450 From °C to 550 ° C, the rolling temperature of the hot rolling treatment is 350 ° C to 450 ° C, and the two cutting rates of the hot rolling treatment are 40% to 60% and 60% to 66%, respectively. Then, the hot rolled sheet is subjected to a cold rolling step to form a cold rolled sheet. Further, the cold-rolled sheet is subjected to a final heat treatment step to obtain a high surface quality aluminum-magnesium-niobium alloy sheet.

According to an embodiment of the invention, the temperature of the homogenization step is from 550 ° C to 580 ° C, and the time of the homogenization step is at least 9 hours.

According to an embodiment of the invention, the preheat treatment time is at least 2 hours.

According to an embodiment of the present invention, the final heat treatment step comprises subjecting the cold-rolled sheet to a solution treatment at 570 ° C for 30 seconds, and subjecting the solution-treated sheet to water quenching treatment.

According to an embodiment of the invention, the aluminum embryo comprises a plurality of impurities, and the individual content of the impurities is less than 0.05 wt.%.

According to an embodiment of the present invention, the surface grain of the high surface quality aluminum-magnesium-niobium alloy sheet is uniformly dispersed and non-directionally arranged.

According to an embodiment of the present invention, between the foregoing homogenization step and the hot rolling step, the manufacturing method of the present invention further comprises the step of shaving the aluminum embryo.

According to the above aspect of the present invention, a high surface quality aluminum-magnesium-niobium alloy sheet is obtained which is obtained by the above-described method for producing a high surface quality aluminum-magnesium-niobium alloy sheet, the surface of which is uniformly dispersed and Non-directional array of grain patterns.

The high surface quality aluminum-magnesium-niobium alloy sheet of the invention and the manufacturing method thereof are made by using the aluminum embryo of a specific composition, the specific pre-heat treatment temperature, the rolling temperature and the reduction rate of the hot rolling step to obtain the surface rope streaks. Obvious aluminum-magnesium-niobium alloy sheet. The above-mentioned aluminum-magnesium-niobium alloy sheet can further have good post-baking strength to provide a wider range of applications in the automotive industry.

200‧‧‧ method

210‧‧‧ Providing aluminum embryos

220‧‧‧Homogeneization steps for aluminum embryos

230‧‧‧ Hot rolling step for aluminum blanks

240‧‧‧Cold rolling steps for hot rolled sheets

250‧‧‧The final heat treatment step of cold rolled sheet to obtain high surface quality aluminum-magnesium-niobium alloy sheet

From the following detailed description in conjunction with the drawings, There is a better understanding of the aspects of the invention.

[Fig. 1] an aluminum-magnesium-niobium alloy sheet having a rope-like stripe on a surface after stretching and deformation;

2 is a schematic flow chart showing a method of manufacturing a high surface quality aluminum-magnesium-niobium alloy sheet according to an embodiment of the present invention.

An object of the present invention is to provide a method for producing a high surface quality aluminum-magnesium-niobium alloy sheet by subjecting an aluminum blank having a specific composition to a hot rolling step to obtain uniform dispersion of surface crystal grains and non-directional arrangement. High surface quality aluminum-magnesium-niobium alloy sheet. In addition, the high surface quality aluminum-magnesium-niobium alloy sheet of the present invention can further have good post-baking strength to expand the application range of the obtained aluminum-magnesium-niobium alloy sheet in the automobile industry.

The term "uniformly dispersed and non-directional arrangement" as used herein means that the arrangement of the surface grains of the aluminum-magnesium-niobium alloy sheet does not cause a distribution of the Roping strip along its rolling direction as shown in FIG. .

The aluminum embryo having a specific composition referred to herein as the present invention may include 0.8% by weight (wt.%) to 1.5% by weight of bismuth, 0.25 wt.% to 0.7 wt.% of magnesium, 0.1 wt.% to 0.5 wt. % of iron, 0.01 wt.% to 0.2 wt.% of manganese, a total amount of less than 0.15 wt.% of one or more impurities and the balance being aluminum. In an embodiment, the aluminum embryo comprises a plurality of impurities, and the individual content of the impurities is less than 0.05 wt.%.

In one embodiment, the purpose of adding bismuth is to increase the precipitation of magnesium lanthanum (Mg-Si) strengthening phase (β" after baking of the sheet to improve the baking of the sheet. Post-bake yield strength (PBYS). When the above sheet is applied to the production of a four-door and two-cover of an automobile, it can have sufficient concave resistance. The above effects are particularly remarkable when the cerium content is more than 0.8 wt.%. However, as the content of rhodium increases, coarse magnesia cast and precipitate phases are produced, thereby reducing the sheet's flexibility, especially when the niobium content is greater than 1.5 wt.%.

In one embodiment, the purpose of adding magnesium is to form the aforementioned magnesium lanthanum strengthening phase (β" together with cerium, and the effect is preferably at a magnesium content of 0.25 wt.% or more. However, when the magnesium content is more than 0.7 wt. When % is used, the formability and the bendability of the sheet are deteriorated.

In one embodiment, iron is an impurity component (>0.1 wt.%) which cannot be avoided by a raw material (for example, a primary aluminum ingot), and a trace amount of iron can improve the problem of the rope-like stripe of the obtained aluminum-magnesium-niobium alloy sheet. . However, when the iron content is higher than 0.5 wt.%, coarse and brittle aluminum-iron-manganese-bismuth (Al-(Fe,Mn)-Si) compound will be formed during sheet casting, which not only makes the sheet ductile toughness The deterioration is caused, and since the reinforcing element bismuth is also consumed, the strength of the sheet is also lowered.

In one embodiment, the purpose of adding trace elements manganese based on the homogenization stage can form fine aluminum ferromanganese _{((Mn, Fe) Al 6} ) a dispersed phase (Dispersoids), and therefore can be used to inhibit crystal solid solution at high temperatures The grain grows to avoid the rough orange peel phenomenon caused by the coarse crystal on the surface of the sheet during press forming. However, if the manganese content is more than 0.2 wt.%, similar to the effect of adding too much iron element, there is also a tendency to produce coarse crystal grains.

In one embodiment, for example, raw materials of the aforementioned composition range (primary aluminum ingots and master alloy ingots) may be smelted and subjected to direct quench casting. (Direct Chill Casting; DC) to obtain the aluminum embryo referred to herein as the present invention.

Hereinafter, a method for producing a high surface quality aluminum-magnesium-niobium alloy sheet of the present invention will be described with reference to Fig. 2 . 2 is a schematic flow chart showing a method 200 of fabricating a high surface quality aluminum-magnesium-niobium alloy sheet according to an embodiment of the present invention.

As shown in step 210 of Figure 2, an aluminum embryo comprising the aforementioned chemical composition is provided first. Next, as shown in step 220, the aluminum embryo is subjected to a homogenization step. In one embodiment, the homogenization step can have a temperature of from 550 ° C to 580 ° C and the homogenization step is for a period of at least 9 hours. In one example, the time of the homogenization step can be, for example, from 9 hours to 12 hours. When the time of the homogenization step is insufficient, the solid solution amount of the obtained aluminum-magnesium-niobium alloy sheet is insufficient, resulting in poor strength after baking.

Next, as shown in step 230, the aluminum blank after the completion of the homogenization step is subjected to a hot rolling step to form a hot rolled sheet. The hot rolling step comprises: preheating the aluminum blank; and, after the preheating, hot rolling the aluminum blank. In some embodiments, the preheat treatment may have a temperature of from 450 °C to 550 °C. In some embodiments, the finishing temperature of the hot rolling treatment may be from 350 ° C to 450 ° C. In still other embodiments, the final two reduction rates of the hot rolling process are 40% to 60% and 60% to 66%, respectively.

It should be noted that the preheating treatment of the present invention controls the amount of solid solution/precipitation and the rolling temperature of the sheet. In addition, the hot rolling treatment of the present invention focuses on the entire hot rolling treatment process at a relatively low temperature (i.e., at the time of the last two hot rolling), performing high reduction rate hot rolling to obtain recrystallization of the hot rolled sheet. The required driving force (meaning that the grains in a disordered orientation have a high nucleation density and a suitable grain growth rate) can form a dense, uniformly dispersed, non-directionally arranged surface grain. The hot-rolled sheet material having the surface grains of the above-described distribution manner maintains the aforementioned distribution pattern after the subsequent treatment (for example, the cold rolling step and/or the final heat treatment step), so that the manufacturing method of the present invention can improve the conventional aluminum. The surface of the magnesium-niobium alloy sheet has a distribution of rope-like stripes.

Therefore, if the above-mentioned finish rolling temperature is too low and the grain growth is too slow, the crystal may not be completely recrystallized, so that the aluminum-magnesium-niobium alloy sheet thus produced still has a problem of crystal grains having a band-like distribution on the surface. If the above-mentioned finish rolling temperature is too high or the amount of reduction is insufficient, the number of crystal nucleation is reduced and the growth rate is too fast, so that the prepared aluminum-magnesium-niobium alloy sheet will be derived from the deformed surface orange peel due to the coarse crystal. problem. In addition, too high a reduction amount is difficult to achieve in the process, and the reduction amount of the present invention is a specific range selected in consideration of the cost and quality of mass production.

In an embodiment, the pre-heat treatment described above may be performed, for example, for at least 2 hours. If the preheating time is less than 2 hours, the predetermined effect of controlling the solid solution/precipitation amount and the rolling temperature cannot be achieved. However, although the upper limit value of the preheating time is not particularly limited, the long-time preheating treatment increases the production cost of the aluminum-magnesium-niobium alloy sheet.

Next, as shown in step 240, the hot rolled sheet is subjected to a cold rolling step to form a cold rolled sheet. In one embodiment, the cold rolling step may, for example, roll the hot rolled sheet to a thickness of about 1 mm, although the invention is not limited thereto.

Thereafter, as shown in step 250, the cold rolled sheet is finally The heat treatment step is performed to obtain the high surface quality aluminum-magnesium-niobium alloy sheet of the present invention. In one embodiment, the final heat treatment step comprises: subjecting the cold rolled sheet to a solution treatment at 570 ° C for 30 seconds; and subjecting the solution treated sheet to water quenching treatment.

In some embodiments, between the foregoing homogenization step and the hot rolling step, the manufacturing method of the present invention may further comprise a step of shaving the aluminum embryo. The planing step referred to herein is to remove the brittle layer of the surface of the aluminum blank after homogenization treatment to further improve the surface quality of the obtained aluminum-magnesium-niobium alloy sheet.

Another object of the present invention is to provide a high surface quality aluminum-magnesium-niobium alloy sheet obtained by the above-described production method, the surface of which has a uniformly dispersed and non-directional arrangement of crystal grains.

Hereinafter, specific embodiments of the method for producing a high surface quality aluminum-magnesium-niobium alloy sheet of the present invention and their effects will be described using a plurality of examples.

Example 1

Example 1 is an aluminum embryo made of a 6000 series aluminum alloy, and the aluminum embryo is subjected to a homogenization step for 9 hours at 550 ° C and cooled to room temperature. Next, after the aluminum embryo is peeled and shaved, the aluminum embryo is preheated at 500 ° C for 2 hours, and the aluminum blank is hot rolled to a hot rolled sheet of about 6 mm thick, wherein the last two cuts of the hot rolling treatment The rates were 44% and 66%, respectively, and the finishing temperature was 370 °C. Thereafter, the hot rolled sheet was cold-rolled to a cold rolled sheet of about 1 mm thick, and further subjected to a solution treatment and a water quenching treatment at 570 ° C for 30 seconds to obtain a high surface quality aluminum magnesium niobium alloy sheet of Example 1. material. Aluminum-magnesium-bismuth alloy sheet The material was tested for surface rope streaks and post-baking strength, and the evaluation results are shown in Table 1.

Examples 2 to 6 and Comparative Examples 1 to 2

Examples 2 to 6 and Comparative Examples 1 to 2 were carried out in the same manner as in Example 1, except that Examples 2 to 6 and Comparative Examples 1 to 2 were changed in the process conditions used. The specific process conditions and evaluation results of Examples 2 to 6 and Comparative Examples 1 to 2 are shown in Table 1, and are not described herein.

Evaluation method

Rope stripe

The rope-like stripe of the present invention is obtained by slightly grinding the surface of the aluminum-magnesium-niobium alloy sheet obtained by stretching the surface of the obtained aluminum-magnesium-niobium alloy sheet by 10% in the vertical rolling direction (the ink may be previously coated with ink). Simulate the state after painting), and then visually judge whether there are rope-like stripes extending along the rolling direction thereof; wherein the values are 0 to 4, 0 is cordless, and 1 to 2 is not obvious. 3 to 4 are obvious for the rope-like stripes. The evaluation result of the rope-like stripe of the present invention is preferably 0 to 2.

2. After baking strength

The post-baking strength of the present invention is that the prepared aluminum-magnesium-niobium alloy sheet is first subjected to a 2% pre-tensile strain, and then baked at 170 ° C, and then JIS No. 5 according to JIS Z2241 test method. The test piece is obtained after the tensile test; wherein "◎" stands for good strength after baking, and "O" stands for baking. The strength after baking is OK, "△" means that the strength after baking is acceptable, and "X" means that the strength after baking is poor.

Please refer to Table 1. Examples 1 and 2 of Table 1 increased the reduction ratio of the last hot rolling from 54% (comparative example) to more than 60% to increase its storage energy (process strain energy), thus the surface ropes of Examples 1 and 2 The stripes are not obvious. In the second embodiment, although the surface rope stripe of the embodiment 2 is superior to the embodiment 1, since the preheating temperature of the embodiment 2 is lower, the alloy solid solution amount thereof is relatively insufficient, so that the embodiment 2 is The strength after baking is slightly degraded, but it is still acceptable.

Further, Examples 3 and 4 adjust the homogenization temperature and time and the cropping rate of the penultimate pass of the hot rolling process. The higher homogenization temperature and the longer homogenization treatment increase the amount of solid solution of the alloy in the aluminum embryo. In addition, increasing the reduction rate of the last two passes effectively improves the post-baking strength and the grade of the rope-like stripes of the aluminum-magnesium-niobium alloy sheet.

Further, Example 5 further increased the finish rolling temperature to 400 ° C. As shown in Table 1, in addition to increasing the rope-like stripe grade on the surface of the aluminum-magnesium-niobium alloy sheet, the original high post-baking strength was maintained. Example 6 The composition of the aluminum embryo was changed and the same process conditions as in Example 5 were applied, and the obtained aluminum-magnesium-niobium alloy sheet had the advantages of eliminating the string-like streaks and excellent post-baking strength.

In contrast, Comparative Examples 1 and 2 used the reduction ratio outside the scope of the present invention, and the surface string streaks were not able to reach an acceptable level, and even the strength after baking was not good.

By applying the method for manufacturing a high surface quality aluminum-magnesium-niobium alloy sheet of the present invention, the grain growth direction and speed in the hot-rolled sheet can be controlled by a specific composition of the aluminum embryo and a hot rolling step of a specific process condition, thereby The surface of the obtained aluminum-magnesium-niobium alloy sheet has crystal grains which are uniformly distributed and non-directionally arranged, so that no streaky stripes are distributed on the surface of the aluminum-magnesium-niobium alloy sheet. In addition, the obtained aluminum-magnesium-niobium alloy sheet can further have good post-baking strength to enhance its application in the automotive industry.

While the invention has been described above in terms of several embodiments, it is not intended to limit the scope of the invention, and the invention may be practiced in various embodiments without departing from the spirit and scope of the invention. The scope of protection of the present invention is defined by the scope of the appended claims.

Claims (8)

A method for producing a high surface quality aluminum-magnesium-bismuth alloy sheet, comprising: providing an aluminum embryo comprising: 0.8% by weight (wt.%) to 1.5% by weight of bismuth; 0.25 wt.% to 0.7 wt.% of magnesium ; 0.1 wt.% to 0.5 wt.% of iron; 0.01 wt.% to 0.2 wt.% of manganese; a total amount of less than 0.15 wt.% of one or more impurities; and the balance of aluminum; a homogenization step; performing a hot rolling step on the aluminum blank to form a hot rolled sheet, wherein the hot rolling step comprises: preheating the aluminum blank, wherein the preheating temperature is 450 ° C to 550 And a hot rolling treatment of the aluminum blank, wherein one of the hot rolling treatments has a rolling temperature of 350 ° C to 450 ° C, and the two cutting rates of the hot rolling treatment are 40% to 60% and 60, respectively. % to 66%; performing a cold rolling step on the hot rolled sheet to form a cold rolled sheet; and subjecting the cold rolled sheet to a final heat treatment step to obtain the high surface quality aluminum magnesium tantalum alloy sheet . The method for producing a high surface quality aluminum-magnesium-niobium alloy sheet according to claim 1, wherein the temperature of the homogenization step is one It is from 550 ° C to 580 ° C and one of the homogenization steps is at least 9 hours. The method for producing a high surface quality aluminum-magnesium-niobium alloy sheet according to claim 1, wherein the pre-heat treatment is at least 2 hours. The method for producing a high surface quality aluminum-magnesium-niobium alloy sheet according to claim 1, wherein the final heat treatment step comprises: subjecting the cold-rolled sheet to a solution treatment at 570 ° C for 30 seconds; The cold-rolled sheet which has been solution treated is subjected to a water quenching treatment. The method for producing a high surface quality aluminum-magnesium-niobium alloy sheet according to claim 1, wherein the aluminum embryo comprises a plurality of impurities, and the individual content of the impurities is less than 0.05 wt.%. The method for producing a high surface quality aluminum-magnesium-niobium alloy sheet according to the first aspect of the invention, wherein the surface fineness of the high surface quality aluminum-magnesium-niobium alloy sheet is uniformly dispersed and non-directionally arranged. The method for producing a high surface quality aluminum-magnesium-niobium alloy sheet according to claim 1, wherein between the homogenization step and the hot rolling step, the manufacturing method further comprises a step of shaving the aluminum embryo . High surface quality aluminum-magnesium-niobium alloy sheet, which is rooted The method for producing a high surface quality aluminum-magnesium-niobium alloy sheet according to any one of claims 1 to 7, wherein the surface of the high surface quality aluminum-magnesium-niobium alloy sheet has uniform dispersion and no Directional arrangement of grain patterns.