JP2011208251A - Aluminum alloy extruded member excellent in bending crush resistance and corrosion resistance - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide an aluminum alloy extruded member that is excellent in both of bending crush resistance and corrosion resistance required for an energy-absorbing member for an automobile, even if the collision conditions of an automobile are made severe.SOLUTION: The Al-Mg-Si aluminum alloy extruded member comprises, by mass, 0.60 to 1.20% Mg, 0.30 to 0.95% Si, 0.01 to 0.40% Fe, 0.20 to 0.45% Mn, 0.001 to 0.65% Cu, 0.001 to 0.10% Ti, 0.10 to 0.20% Zr and the balance being Al and unavoidable impurities, wherein the contents of the Mg and Si satisfy the relations: Mg(%)≤1.73×Si(%)+0.2 and Mg(%)≥1.73×Si(%)-0.2. The extruded member has an almost rectangular hollow section with a thickness of 2-7 mm, and the 0.2% proof stress of 270-330 MPa. The main structure in the thickness direction section is a fibrous structure, and the thickness of a recrystallized structure in a surface layer is ≤500 μm on each side.

Description

  The present invention relates to an Al—Mg—Si-based aluminum alloy extruded material excellent in bending crushability and a method for producing the same (hereinafter, aluminum is also simply referred to as Al). In addition, although the aluminum alloy extruded material said by this invention means the extruded material hot-extruded, the member after assembled | attached as a vehicle body reinforcing material (energy absorption member) mentioned later is also included. Hereinafter, the Al—Mg—Si system is also referred to as 6000 system.

  As is well known, many body reinforcement members (energy absorbing members) are provided in the automobile body. For example, as is well known, a bumper reinforcing material (also called a bumper reinforcement or a bumper armchair) is used as a strength reinforcing material inside a bumper attached to the front end (front) and rear end (rear) of a vehicle body. Is provided. The bumper reinforcing member has a substantially rectangular cross-sectional shape, and as is well known, is disposed between the bumper and the vehicle body so as to extend in a substantially horizontal direction with respect to the vehicle body and parallel to the vehicle width direction. The bumper and the stay or the crash box behind the bumper constitute an energy absorbing member against the collision of the vehicle body.

  The support structure for the bumper reinforcing material is such that a front side member or a rear side member such as a front side member or a rear side member that extends in the vehicle body length direction from a rear surface with respect to the collision surface via a support member such as a hollow structure having a substantially rectangular cross section. Connected and fixed to the frame. With such a support structure, the bumper reinforcing member absorbs collision energy by crushing and deforming (lateral crushing) in the lateral direction (cross-sectional direction and width direction) against the collision of the vehicle body, and protects the vehicle body. In other words, the bumper reinforcement does not cause damage or scattering when a heavy load is applied during a vehicle collision, and the applied collision energy is loaded by bending deformation in the longitudinal direction or crushing deformation of the cross section (lateral crushing). The ability to absorb energy is required.

  Such functions and support structures are basically the same for other automobile body reinforcements such as door guard bars (door beams, door reinforcements). This door guard bar is provided inside the door to protect the occupant by preventing the door from entering the passenger compartment when it is collided from the side of the vehicle body. In the lateral direction (in the width direction), the cross section undergoes crushing deformation (lateral crushing) to absorb the collision energy.

   In recent years, in order to reduce the weight of these reinforcing materials, instead of steel materials conventionally used, high-strength aluminum alloy extruded materials such as 6000 series and 7000 series (extruded profiles having the same cross-sectional shape in the longitudinal direction, Hereinafter, it is also referred to as an extruded profile). An aluminum alloy is superior in energy absorption performance in the case of the same weight of reinforcing material as compared with steel or the like. In addition, the aluminum alloy extruded material having the same cross-sectional shape in the longitudinal direction can efficiently and in large quantities produce a substantially rectangular hollow cross-sectional structure with excellent strength and rigidity as a reinforcing material. It is. For this reason, an aluminum alloy extruded material is suitable for the reinforcing material as an energy absorbing member for a vehicle body.

  Here, among the high-strength aluminum alloys described above, when a 6000 series aluminum alloy is used as the reinforcing material, there are various advantages over other aluminum alloys. The 6000 series aluminum alloy basically includes only Si and Mg, and has excellent age hardening ability. For this reason, at the time of molding such as bending, the moldability is ensured by reducing the yield strength, and the strength is increased by age hardening by heating at a relatively low temperature artificial aging (curing) treatment such as paint baking after molding. BH properties (bake hardness, artificial age hardening, paint bake hardenability) that can improve and secure the required strength.

  Further, the 6000 series aluminum alloy has a relatively small amount of alloy elements as compared to a 7000 series aluminum alloy having a large amount of alloy such as Mg and Zn. For this reason, when the scraps of these 6000 series aluminum alloys 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. Furthermore, 6000 series aluminum alloy plates are often used for automobile body panels such as hoods, fenders, doors, roofs, trunk lids and the like because of the aforementioned characteristics. For this reason, when disassembling and recycling an automobile body, if the reinforcing material targeted by the present invention is also a 6000 series aluminum alloy of the same type as these body panels, the melting raw material can be used rather than a foreign alloy mixed therein. It is easy to sort and recycle.

  In order to use such a 6000 series aluminum alloy extruded material as the reinforcing material, various proposals have been conventionally made in order to improve the lateral crushability as the reinforcing material and to improve the bending workability to the reinforcing material. It was.

  For example, in Patent Document 1, a 6000 series aluminum alloy billet such as 6063 is homogenized, extruded, cooled, and subjected to aging treatment to produce an aluminum alloy extruded material. It has been proposed to set aging treatment conditions so that the 2% proof stress is 120 to 140 MPa and the elongation is 12% or more. In this method, it is intended to obtain an aluminum extruded material having 0.2% proof stress and elongation optimum for bending processing, small variation in bending processing accuracy and proof stress value, and no buckling even in bending processing such as push-through. Yes.

  Patent Document 2 proposes to improve the bending workability by making the structure of the extruded material of 6000 series aluminum alloy an equiaxed grain structure. In this patent document, in order to obtain an equiaxed grain structure, the contents of Mg and Si are stoichiometrically equivalent, and transition elements such as Mn, Cr, Zr, etc. that promote the fibrous structure are used as the example level. The total amount is regulated to 0.1% or less, extruded at an extrusion temperature of 500 ° C. or higher, and subjected to water quenching (forced cooling) immediately after the extrusion. Thus, an equiaxed grain structure having an average crystal grain size of 100 μm or less and an aspect ratio of the crystal grains (ratio between the length of the crystal grains in the extrusion direction and the length in the thickness direction) of 2 or less is obtained.

  On the other hand, in Patent Document 3, conversely, the structure is not the equiaxed grain structure but a fibrous crystal grain structure (fibrous structure) elongated in the extrusion direction to improve the bending workability of the hollow extruded shape. It has been proposed. In this Patent Document 3, transition elements such as Mn, Cr, Zr and the like are included in a relatively large amount of 0.45 to 0.53% in a total amount at an example level, extruded at an extrusion temperature of 500 ° C. or higher, and extruded. Immediately after that, it is manufactured by water quenching (forced cooling) immersed in a water quenching tank. Thereby, in the Example, 0.25 proof stress of 294 MPa or less is obtained.

  On the other hand, as an energy absorbing member that requires crushing characteristics (vertical crushing) in the axial (longitudinal) direction of extruded materials such as side members and bumper stays, it prevents Euler buckling (bending in a U-shape). It is also known that the tissue is the above fibrous structure in order to be excellent as a bellows-like deformation form (see Patent Documents 4 and 5). In Patent Document 4, the structure of a 6000 series aluminum alloy extruded material composed of stoichiometrically balanced Mg and Si is defined as the fibrous structure. Since Mg and Si are stoichiometrically balanced, an extruded material that tends to have a recrystallized structure is used. In this patent document, transition elements such as Mn, Cr, and Zr are added at a total amount of 0.5 at an example level. %, And is extruded at an extrusion temperature of 500 ° C. or higher, and water-quenched immediately after extrusion to produce a fibrous structure.

  In Patent Document 5, the composition of the extruded material is an excess Si type, and transition elements such as Mn, Cr, Zr and the like are included in a comparatively large amount of 0.25 to 0.48% in a total amount at an example level. The aluminum alloy composition. And in the said patent document, extrusion is performed at the extrusion temperature of 500 degreeC, and it is set as the fibrous structure which controlled the thickness and crystal grain size of the surface recrystallized layer (GG layer). The extruded material is excellent not only in vertical crushing but also in lateral crushing.

JP 2001-316788 A JP 2002-241880 A JP-A-5-171328 Japanese Patent Laid-Open No. 9-256096 JP 2003-183757 A

  Actually, when a 6000 series aluminum alloy extruded material is used as a vehicle body reinforcing material such as a bumper reinforcing material or a door guard bar, the collision load from the substantially horizontal direction is more locally applied to the impacting material of the reinforcing material. Many types of collisions are concentrated. In such a collision mode, even if it is a fibrous structure as in Patent Documents 3 to 5, or an equiaxed grain structure as in Patent Document 2, the 6000 series aluminum alloy extruded material is There is still a problem that the bending crushability, which is important for improving the lateral crushability, tends to be insufficient.

Typical examples of such collision modes include pole collision and offset collision. In the case of such a collision mode, in particular, a collision load from a substantially horizontal direction is concentrated locally on the reinforcement material, so that the vehicle body reinforcement material such as a bumper reinforcement material is longer than the collision portion (collision load load portion). It tends to bend in the direction and damage the car body.
As described above, when the collision condition of the automobile becomes severe, it is necessary to further improve the bending crushability of the extruded material of the 6000 series aluminum alloy. However, even if the fibrous structure has a relatively high strength as described above, there is a great limitation in improving the bending crushability that can cope with this. This is exactly the same not only in the fibrous structure but also in the equiaxed grain structure as in Patent Document 2.

  On the other hand, in order to improve the bending crushability of the reinforcing material, not only the strength of the material but also the device of the cross-sectional shape of the extruded material (reinforcing material) is effective. However, depending on the magnitude of the impact load, the cross-sectional shape is not only a rectangular hollow cross section with a mouth shape, but also a rectangular hollow cross section of a type in which the cross-sectional shape is reinforced by providing a middle rib or a middle rib such as an eye shape or a square shape. There is also a great possibility that the bumper reinforcement lacks the bending crushability, which is important for improving the lateral crushability.

  For this reason, in fact, as an energy absorbing member for lateral crushing (a lateral crushing property is required) such as a bumper reinforcing material and a door guard bar, a 7000 series aluminum alloy extruded material having higher strength than a 6000 series aluminum alloy extruded material. The material is still used as mainstream. However, since this 7000 series aluminum alloy extruded material has many alloy components, it is difficult to recycle and the manufacturing cost is high. There is also a problem that the corrosion resistance is inferior to that of the extruded material of 6000 series aluminum alloy

  The present invention has been made paying attention to such circumstances, and its purpose is to provide bending crushability required as an automobile body reinforcing material (energy absorbing member) even when the collision condition of the automobile becomes severe. An object of the present invention is to provide a 6000 series (Al-Mg-Si series) aluminum alloy extruded material excellent in both corrosion resistance and a method for producing the same.

  In order to achieve this object, the gist of the aluminum alloy extruded material excellent in bending crushability and corrosion resistance of the present invention has a thickness of 2 to 7 mm, a substantially rectangular hollow cross section, and a load perpendicular to the extrusion direction. It is an Al—Mg—Si-based aluminum alloy extruded material used for an energy absorbing member that receives and crushes, and in mass%, Mg: 0.60 to 1.20%, Si: 0.30 to 0.95%, Fe: 0.01-0.40%, Mn: 0.20-0.45%, Cu: 0.001-0.65%, Ti: 0.001-0.10%, Zr: 0.10 Each containing 0.20%, and the contents of Mg and Si are Mg (%) ≦ 1.73 × Si (%) + 0.2 and Mg (%) ≧ 1.73 × Si (%) − 0. 2 with the balance being Al and inevitable impurities, 0.2% proof stress is 270-330MP a, the structure in the cross section in the thickness direction of the extruded material is mainly a fibrous structure, and the thickness of the recrystallized structure of the surface layer portion is 500 μm or less on one side.

  By adopting the above composition and structure, in the aluminum alloy extruded material according to the present invention, the bending line of the plate-like specimen obtained by the push bending method defined in JIS Z2248 is the extrusion direction as the bending crushability. In the 180 ° bending test, performance with a limit bend R of 3.0 mm or less at which cracks do not occur is obtained. Further, as the corrosion resistance, a performance in which intergranular corrosion does not occur in a corrosion test by an alternating immersion method defined in the ISO / DIS11846B method can be obtained. The aluminum alloy extruded material is preferably used for an energy absorbing member that receives a load in a direction perpendicular to the extrusion direction and collapses.

  The aluminum alloy extruded material is obtained by homogenizing heat treatment of an Al—Mg—Si-based aluminum alloy cast billet having the above composition at a temperature of 560 ° C. or higher and a temperature of 400 ° C. or lower at an average cooling rate of 100 ° C./hr or higher. Forcibly cooled, and further, the cast billet is reheated so that the temperature of the extruded material on the extrusion outlet side is in a solution temperature range of 500 ° C. or higher, and hot extrusion is performed at an extrusion speed of 5 to 10 m / min. The extruded material on the extrusion outlet side was forcibly cooled at an average cooling rate of 100 ° C./second or more within 16 seconds immediately after the extrusion process, and then this extruded material was further aged to give a 0.2% yield strength of 270 to 270. It can manufacture by setting it as 330 MPa.

  The 6000 series aluminum alloy extruded material according to the present invention has high strength and excellent bending crushability, and is the same energy as the 7000 series aluminum alloy extruded material. It can use suitably for an absorption member. Moreover, corrosion resistance is superior to 7000 series aluminum alloy extruded material.

Test No. 5 is an optical micrograph of a cross section parallel to the extrusion direction of No. 5;

Hereinafter, embodiments of the extruded material of 6000 series aluminum alloy according to the present invention will be specifically described.
(Fibrous structure and surface recrystallized structure)
In the present invention, the structure of the Al—Mg—Si-based aluminum alloy extruded material is mainly a fibrous structure, and the thickness of the recrystallized structure layer formed on the surface layer is limited to 500 μm or less on one side. This is to obtain% yield strength and excellent bending crushability. In the present invention, the fibrous structure mainly means that 50% or more of the plate thickness is a fibrous structure.
(0.2% yield strength)
In the present invention, the 0.2% proof stress of the Al-Mg-Si-based aluminum alloy extruded material is limited to the range of 270 to 330 MPa. The 0.2% proof stress equivalent to that of the 7000-based aluminum alloy extruded material and excellent bending This is to achieve crushability at the same time. Further, when the 0.2% proof stress after aging treatment is less than 270 MPa or more than 330 MPa with the composition of the present invention, the bending crushability is lowered.

(Chemical composition)
The chemical composition of the 6000 series aluminum alloy targeted by the present invention will be described. The 6000 series aluminum alloy targeted by the present invention is required to have excellent properties such as bending crushability and corrosion resistance as an extruded material for the above-mentioned automobile body reinforcement.

  In order to satisfy such a requirement, the composition of the extruded material of 6000 series aluminum alloy (or the cast billet which is the material) targeted by the present invention is mass%, Mg: 0.60 to 1.20%, Si: 0.30-0.95%, Fe: 0.01-0.40%, Mn: 0.20-0.45%, Cu: 0.001-0.65%, Ti: 0.001- 0.10%, Zr: 0.10 to 0.20%, respectively, and the contents of Mg and Si are Mg (%) ≦ 1.73 × Si (%) + 0.2 and Mg (%) ≧ An Al—Mg—Si based aluminum alloy satisfying the relationship of 1.73 × Si (%) − 0.2, the balance being Al and inevitable impurities is used.

  Other elements other than these are basically impurities, and the content (allowable amount) of each impurity level is in accordance with AA to 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. are used as melting materials. There is a high possibility that elements will be mixed. Then, reducing these impurity elements to, for example, below the detection limit itself increases the cost, and a certain amount of allowance is required. Accordingly, the other elements are allowed to be contained within a permissible range in accordance with AA to JIS standards.

The preferable content range and significance of each element in the 6000 series aluminum alloy, or the allowable amount will be described below.
Si:
On the premise that the quantitative relationship with Mg is satisfied, the Si content is set to a range of 0.30 to 0.95%. A preferable content range of Si for obtaining a balanced alloy of Si and Mg is 0.30 to 0.50%. Si, together with Mg, forms aging precipitates that contribute to strength improvement during solid solution strengthening and low-temperature artificial aging treatment in the crystal grains, exhibits age-hardening ability, and is required to be 270 MPa or more necessary as a reinforcing material. It is an essential element for obtaining the required strength (proof strength). When there is too little Si content, the said compound phase cannot be formed at the time of artificial aging treatment, and the said age-hardening ability and required intensity | strength cannot be satisfy | filled. On the other hand, when there is too much Si content, it cannot be set as the above-mentioned balance alloy. Moreover, bending workability etc. also fall and weldability is also inhibited.

Mg:
Assuming that the quantitative relationship with Si is satisfied, the Mg content is set to a range of 0.60 to 1.20%. A preferable content range of Mg for obtaining the above-described balance alloy is 0.60 to 1.0%. Mg forms an aging precipitate that contributes to strength improvement together with Si during solid solution strengthening and artificial aging treatment, exhibits age hardening ability, and has a required strength of 270 MPa or more necessary as a reinforcing material. It is an essential element for obtaining (yield strength). When there is too little Mg content, the said compound phase cannot be formed at the time of artificial aging treatment, and the said age-hardening ability and required intensity | strength cannot be satisfy | filled. Can not show age hardening ability. On the other hand, when there is too much Mg content, it cannot be set as the above-mentioned balance alloy. In addition, bending workability also decreases.

Balance of Mg and Si In the present invention, the content of Mg and Si is Mg (%) ≦ 1.73 × Si (%) + 0.2 and Mg (%) ≧ 1.73 × Si (%) −. The relationship of 0.2 is satisfied. This relation is intended to make the alloy of the present invention a balance alloy in which the contents of Mg and Si are substantially stoichiometrically equivalent among 6000 series aluminum alloys. Desirably, the relationship of Mg (%) ≦ 1.73 × Si (%) + 0.1 and Mg (%) ≧ 1.73 × Si (%) − 0.1 is satisfied.
In an excessive Mg-type 6000 series aluminum alloy extruded material having an excessive Mg content, the bending crushability is lowered. Further, there are demerits that extrudability is lowered, quenching sensitivity is increased, and extrusion productivity is lowered.
In the excessive Si-type 6000 series aluminum alloy extruded material having an excessive Si content, grain boundary precipitates due to Si are coarsened. Therefore, when the Si content exceeds the above relationship, the bending crushability and corrosion resistance of the extruded material as the reinforcing material cannot be improved.

Fe:
Fe has the same function as Mn, Zr, etc., generates dispersed particles (dispersed phase), prevents grain boundary movement after recrystallization, prevents coarsening of crystal grains, and refines crystal grains. effective. Fe is an element that inevitably tends to be mixed in a certain amount (substantial amount) from scrap as a melting raw material. For this reason, content of Fe is taken as 0.01 to 0.40% of range. If the Fe content is too small, these effects are not obtained. On the other hand, when the content of Fe is too large, coarse crystallized products such as Al-Fe-Si crystallized products are likely to be generated, and these crystallized products deteriorate the fracture toughness and fatigue characteristics. A more desirable range is 0.1 to 0.3%.

Mn:
In order to make the structure of the extruded material a fibrous structure elongated in the extrusion direction, the Mn content is set to a range of 0.20 to 0.45%. Mn is a transition element, like Zr, and is necessary to prevent coarsening of crystal grains. Mn generates dispersed particles (dispersed phase) composed of an intermetallic compound such as an Al—Mn system selectively bonded to other alloy elements during the homogenization heat treatment and the subsequent hot extrusion process. Depending on the manufacturing conditions, these dispersed particles are dispersed finely, densely and uniformly, and have the effect of preventing grain boundary movement after recrystallization (pinning effect), preventing coarsening of crystal grains. In addition, the effect of refining the crystal grains is high, and there is an action of making the structure of the extruded material into a fibrous structure. Mn is also expected to increase in strength due to solid solution in the matrix.
If the Mn content is too small, this effect cannot be expected, the surface recrystallized layer is formed thick, and the strength and toughness of the extruded material may be reduced. On the other hand, if Mn is contained excessively, the strength becomes too high, which causes a decrease in the bending crushability as a reinforcing material and the bending workability of the extruded material.

Cu:
Cu contributes to improvement of strength by solid solution strengthening, and also has an effect of significantly accelerating age hardening of the final product during aging treatment. Therefore, 0.001 to 0.65% is contained. If the Cu content is too small, these effects are not obtained. On the other hand, when there is too much content of Cu, the sensitivity of the stress corrosion cracking and intergranular corrosion of an extrusion material structure will be raised remarkably, and corrosion resistance and durability will be reduced. Therefore, the Cu content is within the above range. A more desirable range is 0.2 to 0.5%.

Ti:
Ti has the effect of refining the crystal grains of the ingot to make the extruded material structure fine crystal grains. Therefore, Ti is contained in the range of 0.001 to 0.10%. Moreover, when it contains B which is easy to mix when it contains Ti, it is set as the range of B: 1-300 ppm. If the Ti content is too small, this effect cannot be exhibited. However, when there is too much content of Ti, a coarse crystal precipitate will be formed and it will cause the required characteristics, such as the bending crushability and corrosion resistance as a reinforcing material, and the bending workability of an extrusion material to fall. Therefore, the Ti content is within the above range.

Zr:
Zr, like Mn, is effective (pinning effect) for generating dispersed particles (dispersed phase) made of an intermetallic compound such as an Al—Zr system and preventing coarsening of crystal grains. In addition, when Zr is added, the structure of the extruded material tends to be a fibrous structure elongated in the extrusion direction, like Mn. Therefore, Zr is contained in the range of 0.10 to 0.20%.

(Extruded material cross-sectional shape)
In order for the Al—Mg—Si-based aluminum alloy extruded material to have both a light weight and a bending crushability as a reinforcing material, the cross-sectional shape is preferably a substantially rectangular hollow shape. ) The shape is a rectangular hollow cross section having a substantially mouth shape, and includes both flanges (front wall and rear wall) and both webs (upper and lower side walls connecting both flanges) constituting the mouth shape. To improve the bending crushability of the basic shape of this hollow hollow cross section, it is further reinforced by providing an intermediate rib. The cross-sectional shape is a Japanese shape (one intermediate rib parallel to the upper and lower side walls is provided in the center of the cross section. ), Or a rectangular hollow cross section such as an eye shape (two middle ribs parallel to the upper and lower side walls are provided in the cross section at intervals), and a square shape (a cross middle rib is provided in the cross section).

  Further, the length of both ends of the flange is made longer than the width between the webs, and the flanges and webs bulge outward in addition to the straight shape, or the flanges and webs bulge outward. Or it is good also as circular arc shape dented inward. In addition, the cross-sectional shape of the extruded material (reinforcing material) in the longitudinal direction is not necessarily the same, but a hollow shape in which the cross-sectional shape changes partially or sequentially can be freely selected from the design side of the reinforcing material.

(Wall thickness of extruded material)
As the thickness of the extruded material, a thickness capable of enhancing the bending crushability as a reinforcing material for the automobile body is appropriately selected in relation to the above-described cross-sectional shape. However, the object of the present invention is a reinforcing material that absorbs energy against the collision of the vehicle body, and in order to enhance the bending crushability as the reinforcing material, it is not as thin as a vehicle body panel made of the above-described rolled thin plate. However, it is necessary to increase the thickness. In order to improve the bending crushability, it is better that the wall thickness is thick, but even if it is too thick, the weight increases and the weight cannot be reduced. In this respect, the thickness is preferably selected from a range of 2 to 7 mm. If the thickness is 50% or more of the thickness and the thickness of the layer of the recrystallized structure is 500 μm or less on one side, a high 0.2% proof stress and excellent bending crushability can be obtained. Further, in each of the cross-sectional shapes described above, it is not necessary that the thicknesses of both flanges, both webs, and intermediate ribs are all the same, the flanges and other impacting (loading) side walls are thickened, and the others are thinned. You can devise such as doing.

(Production method)
Next, a method for producing a 6000 series aluminum alloy extruded material according to the present invention will be described below. The extruded material of the present invention refers to an extruded material that has been subjected to appropriate tempering such as quenching and artificial age hardening after hot extrusion.

  In the production process of the extruded material of the present invention, first, an aluminum alloy ingot having the above-mentioned 6000 series component composition is cast into a billet. Next, after the billet is homogenized and heat-treated, the billet is once cooled to a temperature in the vicinity of the following room temperature. And it reheats to solution treatment temperature, it extrudes hot, and it forcibly cools on-line by water cooling from just after extrusion to the temperature near room temperature, It is set as the extruded material of the above-mentioned predetermined cross-sectional shape. This extruded material was also subjected to a solution treatment and a quenching process through a series of hot extrusion processes. Thereafter, after cutting and straightening treatment, the extruded material is subjected to artificial age hardening treatment. In addition, this artificial age hardening treatment may not be performed in advance at the stage of the extruded material, but may be performed by baking and curing the paint after painting the automobile body after assembling to the automobile body as an automobile reinforcing material.

Melting and casting:
In the melting and casting process, the molten aluminum alloy melt-adjusted within the above-mentioned 6000 series component composition range is cast by appropriately selecting a normal melting casting method such as a continuous casting method or a semi-continuous casting method (DC casting method). .

Homogenization heat treatment:
Next, the cast aluminum alloy ingot (billet) is subjected to a homogenization heat treatment. The temperature of the homogenization heat treatment is selected from a temperature range of 500 to 570 ° C. The purpose of this homogenization heat treatment (soaking) is to homogenize the structure, that is, to eliminate segregation in the crystal grains in the ingot structure and to sufficiently dissolve the alloy elements and coarse compounds. By subjecting this alloy to a homogenization heat treatment at 500 to 570 ° C., the precipitation of the added Mn and Zr was obtained in a good state, the recrystallization during extrusion was suppressed, and the structure of the extruded material was elongated in the extrusion direction. It becomes easy to become a fibrous structure, and high bending crushability is obtained. If the temperature of the homogenization heat treatment is lower than 500 ° C., the precipitation of Mn and Zr is insufficient and the above effects cannot be obtained. Further, segregation within the crystal grains cannot be sufficiently eliminated, and this acts as a starting point of fracture, so that the bending crushability, mechanical properties, bending workability, etc. are lowered. On the other hand, if the temperature is higher than 570 ° C., the precipitates of Mn and Zr become coarse and the above effects are lost.

  After this soaking, the cast billet is forcibly cooled to a temperature of 400 ° C. or lower, including room temperature, at an average cooling rate of 100 ° C./hr or higher. The cooling rate of this forced cooling is preferably large (fast), and is performed by forced cooling using a fan or water cooling. If forced cooling to a temperature of 400 ° C. or lower after soaking is performed, thereafter, forced cooling is stopped at this temperature, or after the forced cooling is stopped at this temperature, it is allowed to cool to room temperature, or it is continuously forced to room temperature. The cooling can be freely selected. In the case of normal cooling, the average cooling rate after soaking is about 40 ° C./hr.

Hot extrusion:
Next, the cast billet is reheated so that the temperature of the extruded material on the extrusion outlet side becomes a solution temperature range of 500 ° C. or higher, and hot extrusion is performed at an extrusion speed of 5 to 10 m / min. The extruded material on the side is forcibly cooled at an average cooling rate of 100 ° C./second or more immediately after extrusion, and is used as a tempered material for T5, or T6 (aging) or T7 in combination with artificial aging treatment thereafter. Use an over-aged tempered material. In the tempering treatment of T5, the temperature of the extruded material on the extrusion outlet side is set to a temperature in the solution temperature range of 500 ° C. or more, and the solution treatment is performed online (extrusion process), and then within 16 seconds immediately after the extrusion. A quenching process is performed in which the extruded material is forcibly cooled on-line (extruder exit side) to a temperature close to room temperature.

The temperature at the time of hot extrusion has an advantage that the billet can be heated in a short time at a lower temperature. However, when the temperature of the extruded material on the extrusion outlet side is less than 500 ° C., which is lower than the solution temperature range, the coarse compound of Mg and Si (crystal precipitate) remains in the matrix without dissolving. Thus, it becomes a starting point of fracture and decreases the bending crushability. Therefore, it is preferable to select a lower temperature among these, while the temperature of the extruded material on the extrusion outlet side is set to a solution temperature range of 500 ° C. or higher in consideration of these factors. At this time, the reheating temperature of the cast billet does not necessarily need to be extruded as a solution temperature range of 500 ° C. or more, and even if the reheating temperature of the cast billet is less than 500 ° C., due to the processing heat generated during hot extrusion, The extrusion material temperature on the extrusion outlet side can be set to a solution temperature range of 500 ° C. or higher.
The temperature of the extruded material on the extrusion outlet side is the material surface temperature immediately after the die outlet (distance 0 mm from the outlet). If it is difficult to measure immediately after the die exit, the surface temperature of the material is measured with a contact thermometer at a certain distance from the die exit (the position where the temperature can be measured differs depending on the extrusion press). Using the cooling curve, the temperature immediately after the die exit can be calculated by back calculation.

In addition, forced cooling immediately after extrusion can be performed on-line by combining or combining a spray or shower of mist, water, etc., or a water tank, an air cooling fan, or the like on the line on the exit side of the extruder. . The cooling rate in the case of these forced cooling means is of course as high as 100 ° C./second or more as compared with the cooling rate level of 5 ° C./second or less when the extruded material is allowed to cool, although it depends on the specifications of the equipment. By cooling the extruded material at this cooling rate, the Mg ₂ Si precipitated particles can be prevented from becoming coarse, and the proof stress and the bending crushability can be improved.
This forced cooling is started within 16 seconds from the position where the extruded material is immediately after the die exit (distance 0 mm from the exit). If it is a hollow extruded material having a substantially rectangular hollow cross-section specifically described with respect to the cross-sectional shape of the extruded material and the thickness of the extruded material and has a thickness of 2 to 7 mm, natural cooling until the start of forced cooling can be considered. By starting forced cooling within 16 seconds after extrusion, it is possible to prevent coarsening of Mg ₂ Si precipitated particles and a decrease in yield strength and bending crushability.

The extrusion speed of hot extrusion is set to 5 to 10 m / min. If the extrusion speed is 5 m / min or more, in a general extruder, forced cooling can be started within 16 seconds after extrusion by the forced cooling means arranged on the outlet side. However, when the extrusion speed exceeds 10 m / min, the shape of the middle ribs or the like collapses and it becomes difficult to maintain the cross-sectional shape.
By this T5 tempering treatment, it is possible to omit the step of performing resolution and quenching by separately reheating the extruded material after the extrusion step. However, due to various circumstances and circumstances, instead of this T5 tempering treatment, after the hot extrusion process, the extruded material is separately reheated to a solution temperature range of 500 ° C. or more, and solution treatment and quenching treatment are performed. It is good also as a tempering treatment material of T6 which performs artificial aging treatment.

Aging treatment:
The extruded material is subjected to artificial age hardening after cutting or straightening to a predetermined length. This artificial age hardening treatment is preferably held in a temperature range of 150 to 250 ° C. for a necessary time. The age hardening of the extruded material is adjusted by this holding time, and is appropriately selected from the time for peak aging to maximize the strength and the time for overaging to improve the corrosion resistance for a longer time.

  Next, examples of the present invention will be described. With each component composition shown in Table 1, a 6000 series aluminum alloy extruded material having a cross-sectional shape was manufactured under the conditions shown in Table 2, and as shown in Table 3, the structure of the extruded material was investigated and characteristics (mechanical) Characteristics, bending crushability) were investigated.

More specifically, in the manufacture of the extruded material, billets were cast from the respective aluminum alloy melts having the respective component compositions shown in Table 1. The billet was subjected to homogenization heat treatment at each temperature shown in Table 2 and then cooled to room temperature by forced air cooling with a fan. The cooling rate was 120 ° C./hr as shown in Table 2.
The billet after this homogenization heat treatment was reheated and immediately hot extruded at the extrusion speed (m / min) and extrusion outlet temperature (° C.) shown in Table 2. Then, forced cooling was started online at a position immediately after the die exit (distance 0 mm from the exit) after a lapse of a predetermined time, and cooled to a temperature near room temperature to obtain an extruded material having a cross-section with a die shape. The water cooling means is a water spray as shown in Table 2, and the average cooling rate is about 500 ° C./second. This extruded material was subjected to artificial age hardening treatment under the conditions shown in Table 2.

  The outer shape of the extruded material of the cross-section of the mold is the size for the bumper reinforcement, and in common with each example, each flange (front wall, rear wall) is 40 mm long, 2.3 mm thick, each web The length of the (side wall) and the middle rib was 40 mm, each thickness was 2.0 mm, and the length after cutting was 1300 mm.

  A specimen (plate-shaped test piece) was cut out from the web (side wall) portion of the extruded material after the artificial age hardening treatment, and the structure and properties of the specimen were measured and evaluated. These results are shown in Table 3.

(Sample structure)
About the test material after standing at room temperature for 15 days after the tempering treatment, the average aspect ratio of crystal grains of each test material was measured using SEM (scanning electron microscope) -EBSP (backscattered electron diffraction image). did. Recrystallized structure with an average aspect ratio of 5 or less and a fibrous structure with an average aspect ratio exceeding 5 are obtained, and the thickness of the recrystallized structure of the surface layer (the thicker side of the recrystallized structures on both sides) is obtained. It was. Except for the recrystallized structure of the surface layer part, all had a fibrous structure. In FIG. An optical micrograph of a cross section parallel to the extrusion direction of 5 is shown.

(Sample material properties)
As the characteristics of the test material after standing at room temperature for 30 days after the tempering treatment, 0.2% yield strength (As yield strength: MPa) and elongation (%) were measured, respectively. Also, bending crushability and corrosion resistance were measured and evaluated. These results are also shown in Table 3.

Tensile test:
In the tensile test, a No. 5 test piece (25 mm width × 50 mm length × extruded material thickness) of JISZ2201 was sampled from the test material and subjected to room temperature tension. At this time, the specimen was collected and the tensile direction was taken as the extrusion direction. The tensile speed was 5 mm / min up to 0.2% proof stress and 20 mm / min after proof stress. The measured N number was 5, and each mechanical property was an average of these values.

Bending crushability (bending workability) test:
The specimen (plate-shaped test piece) was subjected to a 180 ° bending test (in a direction perpendicular to the extrusion direction) by the bending method specified in JIS Z2248 so that the bending line is in the extrusion direction, and the outside of the bending corner. The limit bend R (mm) at which no crack was generated at the (tensile side portion) was determined. If this limit bending R is 3.0 mm or less, it is excellent in bending crushability and can be used as a reinforcing material for automobiles.

Corrosion resistance test:
The specimen was subjected to a corrosion test by an immersion method defined in the ISO / DIS11846B method. The test condition was that the extruded material was immersed in an aqueous solution in which NaCl was dissolved at a concentration of 30 g / l and HCl was dissolved at a concentration of 10 ml / l for 24 hours at room temperature. Were examined to determine whether intergranular corrosion cracking occurred. And when the intergranular corrosion cracking has occurred x, not the intergranular corrosion cracking, but when the intergranular corrosion has occurred Δ, when the intergranular corrosion cracking or intergranular corrosion has not occurred ( A case where superficial general corrosion occurred) was evaluated as ◯.

  As shown in Tables 1 and 2, test no. 1-7 are within the composition range of the present invention component including the relationship between the content of Mg and Si described above, and in the condition range defined in the present invention, homogenization heat treatment (soaking temperature, forced cooling), Hot extrusion (extrusion outlet temperature, extrusion speed, forced water cooling immediately after extrusion) and age hardening are performed. For this reason, as shown in Table 3, the recrystallized layer of the surface layer part is 500 μm or less and mainly has a fibrous structure. As a result, test no. Nos. 1 to 7 are excellent in mechanical properties such as strength (0.2% yield strength of 270 MPa or more) and elongation, and at the same time, excellent in bending crushability and corrosion resistance. These performances indicate that the extruded material has a bending crushing property that can cope even when the collision conditions of the automobile such as pole collision and offset collision become severe as a reinforcing material. Moreover, it has shown that it is excellent also in the corrosion resistance requested | required as a reinforcing material.

In contrast, test no. As for 8-15, the component composition of Table 1 or the manufacturing conditions of Table 2 are outside the scope of the present invention. For this reason, either or both of the proof stress and the bending crushability are test numbers. It is inferior to 1-7.
Test No. As for 8-10, the manufacturing conditions of Table 2 are outside the scope of the present invention. Test No. In No. 8, since the time until the start of forced cooling after extrusion is too long, the precipitates are coarsened and the proof stress is low, and the coarse precipitates are also densely precipitated at the grain boundaries, resulting in poor bending crushability. Test No. In No. 9, since the soaking temperature is too high, the precipitates of Mn and Zr are coarsened, the thickness of the recrystallized layer is increased, the yield strength is low, and the bending crushability is also inferior. Test No. In No. 10, since the soaking temperature is too low, the recrystallization layer becomes thick due to insufficient precipitation of Mn and Zr, the yield strength is low, and the bending crushability is also inferior.

  On the other hand, test no. 11 to 15 are alloy nos. The component composition of 6-10 is outside the scope of the present invention. Test No. 11 is alloy no. Since the Mn content of 6 is small, the thickness of the recrystallized layer is increased and the yield strength is low. Test No. 12 is alloy no. Since there is much Mn content of 7, strength becomes high too much and bending crushability is inferior. Test No. 13 is alloy no. Since the Zr content of 8 is small, the thickness of the recrystallized layer is increased and the yield strength is low. Test No. 14 is an alloy no. Since there is much Zr content of 9, intensity | strength becomes high too much and bending crushability is inferior. Test No. 15 is an alloy no. Since the Mg content of 10 is large and the Mg and Si balance is excessive, the strength becomes too high and the bending crushability is poor.

Claims (2)

An Al—Mg—Si-based aluminum alloy extruded material used for an energy absorbing member that has a thickness of 2 to 7 mm, has a substantially rectangular hollow cross section, and is crushed by receiving a load in a direction perpendicular to the extrusion direction, , Mg: 0.60 to 1.20%, Si: 0.30 to 0.95%, Fe: 0.01 to 0.40%, Mn: 0.20 to 0.45%, Cu: 0.001 -0.65%, Ti: 0.001-0.10%, Zr: 0.10-0.20%, respectively, and the content of Mg and Si is Mg (%) ≦ 1.73 × Si ( %) + 0.2 and Mg (%) ≧ 1.73 × Si (%) − 0.2, the balance is made of Al and inevitable impurities, and the 0.2% proof stress is 270 to 330 MPa. The structure in the cross section in the thickness direction of the extruded material is mainly a fibrous structure, and the recrystallized structure of the surface layer portion An aluminum alloy extruded material excellent in bending crushability, characterized by having a thickness of 500 μm or less on one side. In mass%, Mg: 0.60 to 1.20%, Si: 0.30 to 0.95%, Fe: 0.01 to 0.40%, Mn: 0.20 to 0.45%, Cu: 0.001 to 0.65%, Ti: 0.001 to 0.10%, Zr: 0.10 to 0.20%, respectively, and the content of Mg and Si is Mg (%) ≦ 1.73 Al-Mg-Si-based aluminum alloy billet satisfying the relationship of x Si (%) + 0.2 and Mg (%) ≥1.73 x Si (%)-0.2 with the balance being Al and inevitable impurities After the homogenization heat treatment at a temperature of 500 to 570 ° C., the solution is forcibly cooled to a temperature of 400 ° C. or less at an average cooling rate of 100 ° C./hr or more. The cast billet is reheated to a temperature range and hot pressed at an extrusion speed of 5 to 10 m / min. The extruded material on the extrusion outlet side was forcibly cooled at an average cooling rate of 100 ° C./second or more within 16 seconds immediately after the extrusion processing, and then the extruded material was further aged to obtain 0.2% yield strength. The method for producing an extruded aluminum alloy material having excellent bending crushability according to claim 1, wherein the pressure is 270 to 330 MPa.