WO2016140335A1 - Plaque d'alliage d'aluminium - Google Patents

Plaque d'alliage d'aluminium Download PDF

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Publication number
WO2016140335A1
WO2016140335A1 PCT/JP2016/056719 JP2016056719W WO2016140335A1 WO 2016140335 A1 WO2016140335 A1 WO 2016140335A1 JP 2016056719 W JP2016056719 W JP 2016056719W WO 2016140335 A1 WO2016140335 A1 WO 2016140335A1
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Prior art keywords
plate
surface layer
cube
orientation
layer portion
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PCT/JP2016/056719
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English (en)
Japanese (ja)
Inventor
克史 松本
康博 有賀
久郎 宍戸
和史 佐藤
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株式会社神戸製鋼所
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Priority to CN201680006185.4A priority Critical patent/CN107109548A/zh
Priority to US15/541,617 priority patent/US20180023174A1/en
Publication of WO2016140335A1 publication Critical patent/WO2016140335A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/053—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with zinc as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/10—Alloys based on aluminium with zinc as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working

Definitions

  • the present invention relates to a high-strength 7000 series aluminum alloy sheet that is a 7000 series aluminum alloy sheet manufactured by ordinary rolling and excellent in shock absorption.
  • the reinforcing material for automobile structural members such as the bumper reinforcing material and the door beam has already been widely used by using an extruded shape produced by hot extrusion of a 7000 series aluminum alloy.
  • large structural members such as frames and pillars may be made of a rolled plate manufactured by a conventional method such as hot rolling after soaking or further cold rolling the ingot. preferable.
  • 7000 series aluminum alloy rolled plates are difficult to make because of the high alloy, and have not been put to practical use so far.
  • Patent Documents 1 and 2 As an example of control of the texture of a 7000 series aluminum alloy plate, in Patent Documents 1 and 2, in order to increase the strength of the structural material plate and increase the SCC resistance, the ingot is warm-worked after forging.
  • the sheet structure is made finer by repeatedly rolling. This is because, by making the plate structure fine, a large-angle grain boundary with an orientation difference of 20 ° or more, which causes a potential difference between the grain boundary and the grain boundary, which causes a decrease in SCC resistance, is suppressed. This is to obtain a texture in which the 10 ° small-angle grain boundary is 25% or more.
  • Patent Documents 1 and 2 repeat such a special warm rolling because a texture having a large number of such low-angle grain boundaries is used in a normal hot rolling or cold rolling manufacturing method. It is because it cannot be obtained. Therefore, since the process is greatly different from a normal manufacturing method, it is not practical as a method for manufacturing a plate.
  • patent document 3 it is a board for the purpose of providing the 7000 series aluminum alloy board for motor vehicle members which was manufactured with the manufacturing method of the normal board, and was excellent in both the intensity
  • an Al—Zn—Mg-based aluminum alloy plate having a composition containing Zn: 3.0 to 8.0%, Mg: 0.5 to 4.0%, and the balance consisting of Al and inevitable impurities.
  • the average crystal grain size is 15 ⁇ m or less
  • the average total area ratio of crystal grains having the Brass orientation, the S orientation, and the Cu orientation is 30% or more.
  • the main directions are the Brass direction, S direction, Cu It is stipulated to be a bearing.
  • the 0.2% proof stress is set to a high strength of 350 MPa or more, the elongation is increased, the formability can be secured, and the high strength is achieved. It is said that a decrease in SCC resistance can also be suppressed.
  • VDA238-100 Plate Bending Test has been standardized by the German Automobile Manufacturers Association (VDA) for automotive structural members such as frames and pillars. It is required to satisfy the impact absorption (crush characteristics) at the time of automobile collision, which is evaluated by “for metallic materials (hereinafter referred to as VDA bending test)”.
  • the structure of the plate can be a texture with a large tilt angle boundary increased by 3 to 10 ° by suppressing the large tilt grain boundary as in Patent Documents 1 and 2. Further, as in Patent Document 3, even a texture composed of a fibrous structure cannot satisfy the shock absorption (crushing characteristics) at the time of collision of the automobile.
  • an object of the present invention is a 7000 series aluminum alloy plate manufactured by ordinary rolling, and improves impact absorption (crush characteristics) at the time of automobile collision without reducing strength. And providing a 7000 series aluminum alloy plate.
  • the gist of the aluminum alloy sheet of the present invention is, in mass%, containing Zn: 2.0 to 9.0%, Mg: 0.5 to 4.5%, and Cu. : 0.5% or less (including 0%), Zr: 0.15% or less (including 0%), Mn: 0.2% or less (including 0%), Cr: 0.15%
  • the following is (including 0%) and Sc: 0.05% or less (including 0%), respectively, and the balance is an aluminum alloy plate made of Al and unavoidable impurities.
  • the area ratio of the crystal grains having the Cube orientation is [surface layer portion Cube]
  • the area ratio of the crystal grains having the S orientation is [surface layer portion S].
  • the surface of the crystal grains having the Cube orientation When the rate is [plate thickness center portion Cube] and the area ratio of crystal grains having S orientation is [plate thickness center portion S], the surface layer portion is equiaxed recrystallized with an average crystal grain size of 40 ⁇ m or less.
  • the [surface layer portion Cube] is 10% or more
  • the [surface layer portion S] is 10% or more and 40% or less
  • the [sheet thickness center of the [surface layer portion Cube] [Surface layer portion Cube] / [plate thickness center portion Cube] is more than 1.0 and is a ratio of [surface layer portion S] to [sheet thickness center portion S].
  • the surface layer portion and the plate thickness center portion have different textures such that the surface layer portion S] / [plate thickness center portion S] is less than 1.0.
  • the present inventors focusing on the texture of the 7000 series aluminum alloy plate after solution treatment and quenching treatment, the relationship with the shock absorption (crushing property) at the time of automobile collision, which is evaluated by the VDA bending test, was analyzed. .
  • this shock absorption is particularly affected by the texture of the surface layer portion of the plate, and is improved by making the surface layer portion of the plate a specific texture in which Cube is developed.
  • the strength is maintained by making the central portion (plate thickness central portion) of the plate a specific texture in which the S orientation is developed.
  • the shock absorption at the time of a car collision can be achieved without reducing the strength. It was found that can be improved.
  • the surface layer portion and the plate thickness center portion have different textures so that the 7000 series aluminum alloy plate manufactured by normal rolling has both strength and shock absorption. Can do. Accordingly, it is possible to provide a 7000 series aluminum alloy plate suitable for structural members such as the automobiles and railway vehicles, which require such characteristics.
  • the aluminum alloy sheet referred to in the present invention is a cold-rolled sheet that is hot-rolled after the soaking of the ingot and further cold-rolled, and is further subjected to tempering such as solution treatment. It means a 7000 series aluminum alloy plate manufactured by the method. In other words, it does not include a plate manufactured by a special rolling method or manufacturing method in which warm rolling is repeated many times after forging an ingot as in Patent Documents 1 and 2.
  • Such a 7000 series aluminum alloy plate is used as a structural member for automobiles, bicycles, railway vehicles, etc. after being subjected to press molding and processing including stretch flange processing (burring processing, hole expansion processing) and the like.
  • stretch flange processing burring processing, hole expansion processing
  • Aluminum alloy composition First, the chemical component composition of the aluminum alloy sheet of the present invention will be described below, including reasons for limiting each element. In addition,% display of content of each element means the mass% altogether.
  • the chemical composition of the aluminum alloy sheet of the present invention is an Al—Zn—Mg based 7000 series aluminum alloy, which is required for structural members such as automobiles, such as strength and shock absorption (crush characteristics), and SCC resistance. Determined to guarantee properties.
  • the chemical composition of the aluminum alloy sheet of the present invention is Zn by mass: 2.0 to 9.0%, Mg: 0.5 to 4.5%, and Cu: 0.00%. 5% or less (including 0%), Zr: 0.15% or less (including 0%), Mn: 0.2% or less (including 0%), Cr: 0.15% or less (however, (Including 0%) and Sc: 0.05% or less (including 0%), and the balance is made of Al and inevitable impurities.
  • the composition may further contain one or two of Ag: 0.01 to 0.2% and Sn: 0.001 to 0.1% by mass%. In addition to this, or in addition to this, Ti: 0.001 to 0.1% may also be contained by mass%.
  • Zn 2.0 to 9.0% Zn, which is an essential alloy element, together with Mg, forms clusters (fine precipitates) during room temperature aging after solution treatment and improves work hardening characteristics. Moreover, an aging precipitate is formed during the artificial aging treatment to improve the strength. If the Zn content is less than 2.0% by mass, the strength is insufficient, the texture cannot be controlled as prescribed, and the balance between strength and formability may be reduced. On the other hand, if Zn exceeds 9.0% by mass, the grain boundary precipitate MgZn 2 increases and intergranular corrosion easily occurs, and the corrosion resistance deteriorates. Therefore, the lower limit of the Zn content is 2.0%, preferably 3.7%. Further, the upper limit of the Zn content is 9.0%, preferably 8.3%.
  • Mg 0.5-4.5% Mg, which is an essential alloy element, together with Zn, forms clusters (fine precipitates) during room temperature aging after solution treatment, thereby improving work hardening characteristics. Moreover, an aging precipitate is formed during the artificial aging treatment to improve the strength. If the Mg content is less than 0.5%, the strength is insufficient. If the Mg content exceeds 4.5% by mass, casting cracks occur, the rollability of the plate decreases, and it becomes difficult to produce a prototype of the plate. Therefore, the lower limit of the Mg content is 0.5%, preferably 1.4%. Further, the upper limit of the Mg content is 4.5%, preferably 4.3%.
  • Cu 0.5% or less (including 0%), Zr: 0.15% or less (including 0%), Mn: 0.2% or less (including 0%) ), Cr: 0.15% or less (including 0%), and Sc: 0.05% or less (including 0%), respectively.
  • Cu is usually added in many cases because it has an effect of improving the SCC resistance of an Al—Zn—Mg-based alloy and an effect of improving the strength.
  • Zr, Mn, Cr, and Sc are often added to improve the strength by refining the crystal grains of the ingot and the final product plate. For this reason, normally, the probability that the area ratio [surface layer portion Cube] of the crystal grains having the Cube orientation in the surface layer portion cannot be increased by Cu, Zr, Mn, Cr, and Sc as defined in the present invention is high. .
  • Ag 0.01 to 0.2%, Sn: 0.001 to 0.1% Ag and Sn are aging that contributes to strength improvement by artificial aging treatment after molding processing to a structural material Precipitates are closely and finely precipitated, and have the effect of promoting high strength, so they are selectively contained as required. When one or both of these are contained, if the Sn content is less than 0.001% and the Ag content is less than 0.01%, the strength improvement effect is small. On the other hand, when there is too much Sn and Ag content, various characteristics, such as rolling property and weldability, will be reduced. In addition, the strength improvement effect is saturated, and Ag is only expensive. Therefore, Ag: 0.01 to 0.2% and Sn: 0.001 to 0.1% are set.
  • Ti 0.001 to 0.1% Ti, together with B, is an impurity in the rolled plate, but has the effect of refining the crystal grains of the aluminum alloy ingot, so that it is allowed to be contained as a 7000 series alloy within the range specified by the JIS standard. If Ti is less than 0.001%, the effect of crystal grain refinement cannot be obtained. On the other hand, when Ti exceeds 0.1%, a coarse compound is formed and the mechanical properties are deteriorated. Therefore, the upper limit of Ti is 0.1%, preferably 0.05% or less. Further, it is allowed to contain B up to 0.03% with this Ti. When B exceeds 0.03%, a coarse compound is formed and the mechanical properties deteriorate.
  • the 7000 series aluminum alloy plate of the present invention has the same composition and many production steps as the conventional 7000 series aluminum alloy plate and its production method (normal rolling method). For this reason, as the plate structure, a large number of fine nano-sized precipitates are present in the crystal grains, which is the basis for satisfying basic characteristics such as strength and corrosion resistance.
  • These fine nano-level precipitates are the intermetallic compounds of Mg and Zn (composition is MgZn 2 and the like) that are generated in the crystal grains, and include elements corresponding to the composition. It is a finely dispersed phase.
  • Texture Based on the above-mentioned composition of the 7000 series aluminum alloy plate, in the present invention, in order to improve characteristics such as shock absorption (crush characteristics), strength, and corrosion resistance, which are evaluated by a VDA bending test, in an automobile collision.
  • the structure of the 7000 series aluminum alloy plate is controlled.
  • the surface layer portion from the surface of the plate to a depth of 15% of the plate thickness is made an equiaxed recrystallized structure having an average crystal grain size of 50 ⁇ m or less.
  • the average crystal grain size of this surface layer exceeds 50 ⁇ m, or when it becomes an elongated work structure elongated in the rolling direction instead of an equiaxed recrystallized structure (as it is)
  • VDA bendability Impact absorption (crushing properties) is reduced without developing crystal grains having a Cube orientation that improve the strength.
  • the depth of 15% of the plate thickness from the surface of the plate is the depth from the outermost surface of the aluminum matrix of the plate after removing the oxide film on the surface of the plate (test material) by polishing.
  • the grain structure is greatly affected.
  • the texture of the surface layer part from the surface of a board to the depth of 15% of board thickness is prescribed
  • the surface layer portion having this texture exists from the surface of the plate to a depth exceeding 15% of the plate thickness, the surface layer portion is too thick, and the thickness of the center portion of the plate that guarantees the strength is thin. As a result, the high strength of the entire plate cannot be guaranteed.
  • the surface layer portion of the plate mainly has a Cube orientation that is superior in impact absorption (crushing property) to strength.
  • the thickness center portion of the plate has a texture mainly having an S orientation superior in strength to shock absorption (crushing property). That is, in the present invention, the Cube orientation effective for the shock absorption (crushing characteristics) of the surface layer portion of the plate is ensured in its absolute amount, and is made larger than the Cube orientation of the center portion of the plate thickness, thereby the shock absorption. Improve (crush characteristics).
  • an absolute amount of the S orientation effective for improving the strength is secured, and this absolute amount is calculated based on the area ratio of the S orientation of the center portion of the plate thickness and the area of the S orientation of the surface layer portion.
  • the strength of the plate is ensured by prescribing more than the rate.
  • the surface layer portion and the plate thickness center portion of the plate are formed into optimum textures respectively for the shock absorption and strength, and the surface layer portion and the plate thickness center portion A plate having a composite structure in the thickness direction, which has a different texture and action.
  • each area ratio in the surface layer part of Cube orientation and S orientation, and the thickness center part Specifically, in the present invention, among the crystal grains in the surface layer portion of the plate from the surface to a depth of 15% of the plate thickness, the area ratio of the crystal grains having the Cube orientation is defined as [surface layer portion Cube], and the S orientation is obtained. Let the area ratio of a crystal grain be [surface layer part S]. Of the crystal grains in the plate thickness center portion of the plate, the area ratio of the crystal grains having the Cube orientation is [plate thickness center portion Cube], and the area ratio of the crystal grains having the S orientation is [plate thickness center portion S]. ].
  • the [surface layer portion Cube] is set to 10% or more, and the [surface layer portion S] is set to 10% or more and 40% or less.
  • [surface layer portion Cube] / [plate thickness center portion Cube] which is a ratio of the [surface layer portion Cube] and the [plate thickness center portion Cube]
  • [surface layer portion S] And [surface layer portion S] / [plate thickness center portion S] which is a ratio of the above and [plate thickness center portion S]
  • the plate manufactured by a conventional method has a [surface layer portion Cube] / [plate thickness center portion Cube] of 1.0, [surface layer portion S] / [plate thickness center portion S] of 1.0, and a surface layer of the plate.
  • the portion and the plate thickness center portion have the same texture.
  • the upper limit of the [surface layer part Cube] is about 80% from the manufacturing limit.
  • a preferable range of the [surface layer portion Cube] is a range of 10% or more and 80% or less.
  • the [surface layer portion Cube] is less than 10%, the [surface layer portion S] is more than 40%, or the [surface layer portion Cube] / [plate thickness center portion Cube] is 1.0 or less, When there is too little [surface layer part Cube], VDA bendability will fall and the shock absorptivity (crushing characteristic) at the time of a car collision will fall. Further, if the [surface layer portion Cube] / [plate thickness center portion Cube] is 1.0 or less and the [plate thickness center portion Cube] is too much, the [plate thickness center portion S] becomes too small as will be described later. As a result, the strength decreases.
  • the [surface layer portion S] is less than 10%, the [surface layer portion S] / [plate thickness center portion S] is 1.0 or more, and the [plate thickness center portion S] is too small. If the plate thickness center portion S] is too much, the strength decreases.
  • [surface layer portion Cube] / [plate thickness center portion Cube] is 1.2 or more, [surface layer portion S] / [plate thickness]
  • the center portion S] is 0.8 or less, and more preferably, the [surface layer portion Cube] / [plate thickness center portion Cube] is 1.3 or more and the [surface layer portion S] / [plate thickness center portion S] is 0.7.
  • the average crystal grain size and the area ratio of crystal grains having each orientation defined in the present invention are all measured by the EBSP method. More specifically, the surface layer part from the width direction cross section of the cold-rolled sheet or hot-rolled sheet (T4 material) after solution treatment to a depth of 15% of the sheet thickness and the center part of the sheet thickness are sampled respectively. Then, a sample having a surface prepared by mechanical polishing and further by electrolytic polishing following buff polishing is prepared, and crystals of the surface layer portion and the plate thickness center portion by EBSP using SEM or FESEM Orientation measurement and crystal grain size measurement are performed, respectively.
  • the EBSP measurement / analysis system uses EBSP: manufactured by TSL (OIM) or OXFORD (CHANNEL5).
  • tissue of a board is five measurement test pieces (5 place
  • the SEM / EBSP method is widely used as a texture measurement method, and is applied to a scanning electron microscope (Scanning Electron Microscope: SEM) or a field emission scanning electron microscope (Field Emission Scanning Electron Microscope: FESEM).
  • SEM scanning Electron Microscope
  • FESEM Field emission scanning electron microscope
  • This measurement method has a high measurement accuracy because of its high resolution as compared with other texture measurement methods, and has an advantage that the average crystal grain size of the same measurement site of the plate can be simultaneously measured with high accuracy.
  • an EBSP is projected onto a screen by irradiating an electron beam onto a sample of an Al alloy plate set in a lens barrel of the SEM or FESEM (FE-SEM). 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. Each calculated orientation of the crystal is recorded as a three-dimensional Euler angle together with position coordinates (x, y) and the like. Since this process is automatically performed for all measurement points, tens of thousands to hundreds of thousands of crystal orientation data can be obtained at the end of measurement. Details of the crystal orientation analysis method in which the EBSP system is mounted on these SEM or FESEM are described in detail in Kobe Steel Technical Report / Vol. 52 No. 2 (Sep. 2002) P66-70.
  • a texture in a rolled sheet of an aluminum alloy usually includes a Cube orientation, a Goss orientation, a Brass orientation, an S orientation, and a Copper orientation. How these textures are formed differs depending on the processing and heat treatment methods even in the case of the same crystal system.
  • the rolling surface is represented by the rolling surface and the rolling direction, and the rolling surface is represented by ⁇ hkl ⁇ . Expressed and the rolling direction is expressed as ⁇ uvw>. Based on this expression, each direction is expressed as follows.
  • Cube orientation ⁇ 001 ⁇ ⁇ 100> Goss orientation ⁇ 011 ⁇ ⁇ 100> Brass orientation (B orientation) ⁇ 011 ⁇ ⁇ 211> Cu orientation (Copper orientation) ⁇ 112 ⁇ ⁇ 111> S orientation ⁇ 123 ⁇ ⁇ 634> B / G direction ⁇ 011 ⁇ ⁇ 511> B / S orientation ⁇ 168 ⁇ ⁇ 211> P direction ⁇ 011 ⁇ ⁇ 111>
  • deviations (tilt angles) of orientation less than ⁇ 10 ° from these crystal planes belong to the same crystal plane (orientation factor). Further, the boundary between crystal grains in which the orientation difference (tilt angle) between adjacent crystal grains is 5 ° or more is defined as a crystal grain boundary.
  • the surface layer portion [surface layer portion Cube] and [surface layer portion S from the surface of the plate to a depth of 15% of the plate thickness are used.
  • regulated by this invention was computed by making the total area of each crystal orientation (all crystal orientations) from Cube orientation described above into P orientation into 100.
  • the average crystal grain size is also measured and calculated at a grain boundary with an inclination angle of 5 ° or more.
  • an orientation shift of less than ⁇ 5 ° is defined as belonging to the same crystal grain, and a boundary between crystal grains having an orientation difference (tilt angle) of 5 ° or more between adjacent crystal grains is defined as a grain boundary.
  • the 7000 series aluminum alloy sheet of the present invention is a cold-rolled sheet obtained by subjecting an ingot to hot rolling after soaking and further cold rolling, and further subjected to tempering such as solution treatment.
  • Manufactured That is, an aluminum alloy hot rolled sheet having a thickness of about 2 to 10 mm is manufactured through normal manufacturing processes such as casting, homogenization heat treatment, and hot rolling. Subsequently, it is cold-rolled to obtain a cold-rolled sheet having a thickness of 3 mm or less.
  • the 7000 series aluminum alloy plate of the present invention is not manufactured by a special manufacturing method or rolling method in which cold rolling is performed after thin sheet continuous casting such as a twin roll method to omit hot rolling or warm rolling is performed.
  • a special manufacturing method or rolling method in which cold rolling is performed after thin sheet continuous casting such as a twin roll method to omit hot rolling or warm rolling is performed.
  • the soaking conditions and the solution treatment conditions for obtaining the texture defined in the present invention are different from those in the conventional process, as will be described later.
  • 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 aluminum alloy melt adjusted within the above-mentioned 7000-based component composition range. Cast.
  • this homogenization heat treatment is to homogenize the structure, that is, eliminate segregation in crystal grains in the ingot structure.
  • this soaking process has a great influence on the formation of the texture. Therefore, in order to obtain a texture as defined in the present invention, this soaking process is carried out twice soaking instead of the usual one soaking. Or it shall be two-stage soaking.
  • the second soaking means that after the first soaking, the steel is once cooled to a temperature of 200 ° C. or less including room temperature, reheated, and maintained at that temperature for a certain period of time, and then hot rolling is started.
  • the two-stage soaking means cooling after the first soaking, but it is not cooled to 200 ° C. or lower, and after stopping the cooling at a higher temperature, the temperature is maintained as it is.
  • the hot rolling is started after reheating to a higher temperature.
  • the first or first stage of soaking conditions is appropriately selected from a range of a holding time of 2 hours or more in a temperature range of 400 ° C. or higher and lower than the melting point.
  • the average cooling rate is set to 30 ° C./hr or more, preferably 40 ° C./hr or more, in common with the two-stage soaking or the two-stage soaking.
  • the [surface layer portion Cube] can be developed by recrystallization that occurs during the solution treatment, and the [surface layer portion S] can be controlled to an appropriate ratio.
  • the texture specified in the present invention can be made together with the cold rolling conditions and solution treatment conditions described later. it can.
  • the texture defined in the present invention cannot be obtained even if the cold rolling conditions and the solution treatment described below are performed within a preferable range in the normal one-time heat treatment, which is out of the cooling conditions. The possibility increases.
  • the soaking condition for the second or second stage is selected from the range of the holding time of 2 hours or more in the temperature range of the hot rolling start temperature or higher and 500 ° C. or lower. It may be heated and cooled to the hot rolling start temperature, or reheated to the hot rolling start temperature and held in the vicinity thereof. Further, the ingot after soaking at the first stage may be cooled to the hot rolling start temperature and held in the vicinity thereof.
  • the soaking temperature at the second or second stage is preferably lower than the soaking temperature at the first or first stage.
  • the hot rolling start temperature is selected from the range of 350 ° C. to the solidus temperature and hot rolled to obtain a hot rolled sheet having a thickness of about 2 to 10 mm. Annealing (roughening) of the hot-rolled sheet before cold rolling is not always necessary, but may be performed.
  • a cold rolling rate (total cold rolling rate) Is 50% or more.
  • the upper limit of the cold rolling rate is determined by the production limit and is approximately 98%.
  • the number of cold rolling processes is freely selected according to the relationship between the thickness of the hot rolled sheet and the final thickness of the cold rolled sheet, and the sheet (coil) to the cold rolling mill in this cold rolling process. The number of passes can be freely selected.
  • the temperature of the intermediate annealing during the roughing or cold rolling is in the range of 380 to 500 ° C., and an appropriate time is selected according to the sheet feeding conditions in the continuous furnace or batch furnace to be used.
  • the cooling after the intermediate annealing is preferably forced cooling such as air cooling by a fan.
  • the ultimate temperature is desirably 450 ° C. or higher from the viewpoint of ensuring solid solution in the subsequent solution treatment.
  • the ultimate temperature is desirably 420 ° C. or lower.
  • solution treatment After cold rolling, solution treatment is performed as a tempering.
  • the solution treatment is not particularly limited and may be heating and cooling using a normal continuous heat treatment line. However, in order to obtain a sufficient solid solution amount of each element or to refine crystal grains, it is desirable to set a solution treatment temperature of 450 to 550 ° C.
  • the heating (temperature increase) rate during the solution treatment is desirably divided into three stages. First, in the range where the temperature of the plate is 300 ° C. or less, the heating (temperature increase) rate is set to an average range of 0.001 ° C./s to 10 ° C./s. Next, when the temperature of the plate is in the range of 300 ° C. to 450 ° C., the heating (temperature increase) rate is set to an average range of 10 ° C./s to 100 ° C./s. Furthermore, when the temperature of the plate is in the range of 450 ° C. to the solidus temperature, the heating (temperature increase) rate is in the range of 0.001 ° C./s to 10 ° C./s on average.
  • Recrystallization during heating (temperature rise) starts at a lower temperature in the surface layer portion of the plate than in the center portion (center portion) of the plate thickness. For this reason, the [surface layer portion Cube] can be preferentially developed by heating (heating) the plate at a temperature of 300 ° C. or less at the low speed, and the [surface layer portion S is moderately formed. The ratio can be controlled. Also, by heating (heating) the plate at a high temperature in the range of 300 ° C. to 450 ° C., the [plate thickness center S] can be preferentially developed, and the recrystallized grains are coarse. Can be suppressed. When the temperature of the plate is in the range of 450 ° C. to the solidus temperature, solid solution of the strengthening element can be ensured by heating (heating) at the low speed. The average heating rate cannot exceed 100 ° C./s because of the limit of the equipment capacity of the solution treatment furnace.
  • the average cooling (temperature decrease) rate after the solution treatment is preferably 10 ° C./s or more in order to suppress precipitation of coarse dispersed particles during cooling.
  • cooling after the solution treatment is performed by selecting and using a forced cooling means such as air cooling such as a fan, water cooling means such as mist, spraying, immersion, etc., or directly in water or hot water at room temperature to 100 ° C. It is preferable to quench.
  • a forced cooling means such as air cooling such as a fan, water cooling means such as mist, spraying, immersion, etc., or directly in water or hot water at room temperature to 100 ° C. It is preferable to quench.
  • the solution treatment is basically only once, but when the room temperature age hardening has progressed too much, the solution treatment is performed again under the above-mentioned preferable conditions in order to ensure the formability to automobile members and the like. Then, the room temperature age hardening that has progressed too much may be canceled once.
  • the aluminum alloy plate of the present invention is used as a structural member for automobiles, bicycles, railway vehicles and the like after being subjected to press molding and processing including burring processing, hole expansion processing and the like as materials. Further, from the viewpoint of securing moldability, after being molded or processed into these structural members, an artificial age hardening treatment is separately performed to increase the strength as necessary.
  • This artificial age hardening treatment may be performed under general artificial aging conditions (T6, T7), and the temperature and time conditions are based on the desired strength, the strength of the 7000 series aluminum alloy plate of the material, or the progress of aging at room temperature. It is decided freely.
  • T6, T7 general artificial aging conditions
  • the temperature and time conditions are based on the desired strength, the strength of the 7000 series aluminum alloy plate of the material, or the progress of aging at room temperature. It is decided freely.
  • T6 T7 general artificial aging conditions
  • the temperature and time conditions are based on the desired strength, the strength of the 7000 series aluminum alloy plate of the material, or the progress of aging at room temperature. It is decided freely.
  • T6 T7 general artificial aging conditions
  • the temperature and time conditions are based on the desired strength, the strength of the 7000 series aluminum alloy plate of the material, or the progress of aging at room temperature. It is decided freely.
  • an aging treatment at 100 to 150 ° C. is performed for 12 to 36 hours (including an
  • Table 1 shows the composition of the 7000 series aluminum alloy cold-rolled sheet with various compositional changes, as shown in Table 2.
  • the impact absorbability (crush properties) evaluated was evaluated. These results are shown in Table 3 below.
  • the texture of the cold-rolled sheet was controlled mainly by changing the soaking condition and the solution treatment condition as shown in Table 2. Specifically, in common with each example, a 7000 series aluminum alloy molten metal having each component composition shown in Table 1 below is DC-cast, and the resulting ingot is subjected to soaking conditions and hot rolling start temperature shown in Table 2. Was hot rolled to produce a hot rolled sheet having a thickness of 3 to 25 mm. In common with each example, these hot-rolled sheets were held at 500 ° C. for 30 seconds, subjected to roughing (annealing) for forced air cooling, and then cold-rolled under the intermediate annealing conditions shown in Table 2. In common, a cold-rolled sheet having a thickness of 2 mm was obtained.
  • “ ⁇ ” indicates that the content is below the detection limit.
  • the number of cold rollings in each example was 3, and the number of passes per cold rolling process was 3 in common with each example.
  • the intermediate annealing between the cold rolling steps was performed at a heating rate of 200 ° C./min in the case of a continuous annealing furnace, cooling was performed by fan air cooling, and the heating / lowering rate was 30 ° C./hr in the case of a batch annealing furnace. .
  • the intermediate annealing in Table 2 all the examples other than Invention Example 2 in which batch annealing was performed are continuous annealing.
  • these cold-rolled plates were subjected to a solution treatment in which the average heating rate was controlled in three stages according to the temperature range. Holding temperature, holding time, and average cooling rate were also performed under the conditions shown in Table 2 to obtain a T4 material.
  • the T4 material was aged at room temperature for 1 week, and then the sample material was collected to investigate the texture and fine precipitates (reference), and the mechanical properties were examined by a tensile test described later. These results are shown in Table 3, respectively.
  • the texture and average crystal grain size of the T4 material plate specimen are measured by EBSD on the rolling surface of the surface layer and the center of the plate thickness, and the area ratio and crystal grain size of each orientation component grain (circle) Equivalent diameter). Specifically, the measurement was performed by the above-described measurement method on the surface layer portion of the plate-shaped test piece of the T4 material and the rolling surface of the plate thickness center portion. For the measurement, an SEM (JEOL JSM 6500F) manufactured by JEOL Ltd. equipped with an EBSP measurement / analysis system [OIM] manufactured by TSL was used.
  • SEM JEOL JSM 6500F
  • OIM EBSP measurement / analysis system
  • the surface layer portion is a rolled surface at a position up to 15% in the plate thickness direction from the surface of the test piece excluding the oxide film, and the plate thickness center portion is rolled at a position of 50% in the plate thickness direction.
  • the area was 1000 ⁇ m ⁇ 1000 ⁇ m, and the measurement step interval was also 1 ⁇ m in common.
  • the plate test piece of the T6 material or the T4 material was processed into a JIS No. 5 test piece, and a room temperature tensile test was performed so that the tensile direction was parallel to the rolling direction, and the tensile strength (MPa). 0.2% proof stress (MPa) was measured.
  • the room temperature tensile test was performed at a room temperature of 20 ° C. based on JIS2241 (1980), and was performed at a constant speed until the test piece broke at a distance of 50 mm between the ratings and a tensile speed of 5 mm / min.
  • the bending test for evaluating impact absorbability was performed as a VDA bending test in accordance with “VDA238-100 Plate Bending Test for Metallic Materials” in the standards of the German Automobile Manufacturers Association (VDA).
  • VDA German Automobile Manufacturers Association
  • FIG. 1 the plate-like test piece of the T6 material is placed on two rolls arranged parallel to each other with a roll gap, as shown by dotted lines in FIG. .
  • the T6 material plate-shaped test piece is rolled so that the rolling direction and the extending direction of the plate-shaped pushing and bending jig arranged vertically upright are perpendicular to each other.
  • the pressing and bending jig is pressed against the center of the plate-shaped test piece from above to apply a load, and the plate-shaped test piece is bent toward the narrow roll gap (bending) to bend and deform.
  • the center part of the plate-shaped test piece is pushed into the narrow roll gap.
  • the angle of the bending outside of the center part of the plate-like test piece when the load F from the pushing bending jig from the maximum is measured as a bending angle (°), and the magnitude of the bending angle.
  • a bending angle (°)
  • the magnitude of the bending angle Evaluate the shock absorption. The larger the bending angle, the more the plate-like test piece is not crushed in the middle, the bending deformation is continued, and the shock absorption (crushing property) is higher.
  • the symbols shown in FIG. 1 are used to indicate that the plate-shaped test piece has a square shape of width b: 60 mm ⁇ length l: 60 mm, and each of the two roll diameters D is 30 mm.
  • the roll gap L was 4 mm, which is 2.0 times the plate thickness of the plate-shaped test piece.
  • s is the depth of intrusion into the roll gap at the center of the plate-like test piece when the load F is maximum.
  • the plate-like pushing / bending jig presses against the center portion of the plate-like test piece so that the lower end side has a radius of 0.2 mm ⁇ at the tip (lower end). It has a sharp tapered shape.
  • the above bending test was carried out by three plate-like test pieces (three times), and the average value of the bending angles (°) was adopted.
  • a current having a current density of 1 mA / cm 2 was allowed to flow for 24 hours in a state immersed in an aqueous sodium chloride solution (5% by mass), and then the sample was pulled up, and then the cross section of the test piece was cut and polished.
  • the magnification was x100, and a corrosion depth of 200 ⁇ m or less was evaluated as “ ⁇ ” as minor corrosion. Moreover, the case where it exceeded 200 micrometers was evaluated as "x" as big corrosion.
  • each of the inventive examples is within the composition range of the aluminum alloy of the present invention, and is manufactured within the range of the preferred soaking conditions and cold rolling conditions described above.
  • the structure of the T4 material is an equiaxed recrystallized structure in which the average crystal grain size of the surface layer portion from the surface of the plate to a depth of 15% of the plate thickness is 40 ⁇ m or less, and the [surface layer portion Cube] Is 10% or more, and the [surface layer part S] is 10% or more and 40% or less.
  • the [surface layer portion Cube] / [plate thickness center portion Cube] exceeds 1.0 and the [surface layer portion S] / [plate thickness center portion S] is less than 1.0.
  • the T6 material has a 0.2% proof strength of 358 to 391 MPa
  • the VDA bending angle is 67 to 55 °
  • the 0.2% proof strength is 425 to 446 MPa. It has a high level of 44 to 40 °, and has both strength and shock absorption (crushing properties). It also has excellent corrosion resistance.
  • Invention Examples 1 and 2 in Tables 2 and 3 are good examples in which the contents of Mg and Zn are balanced with each other to obtain the required strength, in other words, to control the strength.
  • Inventive Example 2 has a Zn content less than Inventive Example 1 as shown in Table 1, but as shown in Table 3, the 0.2% yield strength is higher than Inventive Example 1. This is because Invention Example 2 balances the contents of Mg and Zn with each other due to the low Zn content, and controls the Mg content more than Invention Example 1 to ensure strength. .
  • Inventive Example 1 has a large Zn content, but the Mg and Zn contents are balanced with each other to reduce the Mg content and control the 0.2% proof stress to be lower than Inventive Example 2. Yes.
  • the alloy composition is not within the scope of the present invention as shown in Table 1, or the alloy composition is within the scope of the present invention, but the ranges of the preferred soaking conditions and cold rolling conditions described above. Each is manufactured. As a result, even if the desired texture cannot be obtained or obtained, the VDA bending angle is low for the strength.
  • Comparative examples 9 to 15 use the same alloy examples 1 and 3 as the invention examples of Table 1. However, as shown in Table 2, these comparative examples have only one soaking (Comparative Example 10), the cooling rate after the first soaking is slow (Comparative Examples 10 to 12), and the cold rolling rate is low. (Comparative Examples 9 and 10), conditions in which manufacturing conditions are preferable, such as each average temperature increase rate in each temperature range of the three stages of solution treatment (Comparative Examples 9, 11, 12, 13, 14, 15) It is off.
  • the VDA bending angle is only a low level of 42 to 37 °, which is the same strength level as the above invention example. It can be seen that it is remarkably lower than the level of the VDA bending angle, and does not have both strength and shock absorption (crush characteristics).
  • Comparative Examples 16 to 23 are manufactured in a preferable condition range except for Comparative Examples 19 and 20, but use Alloy Nos. 9 to 16 in Table 1 and have a small amount of Zn (Alloy No. 9) and a small amount of Mg. (Alloy No. 10), Cu, Zr, Mn, Cr, and Sc are too much (Alloy Nos. 11 to 16).
  • Comparative Example 19 is only one-time soaking
  • Comparative Examples 19 and 20 have a low cold rolling rate
  • Comparative Example 20 has an average rate of temperature increase in each temperature range of the three stages of solution treatment.
  • the preferable condition for the average cooling rate after the solution treatment is also out of the range.
  • the VDA bending angle is only a low level of 53 to 32 °, and the 0.2% proof stress is a strength of 428 to 471 MPa.
  • the VDA bending angle is a low level of 38 to 32 °, which is significantly lower than the level of the VDA bending angle at the same strength level as in the above-described invention example, and the strength and shock absorption (crushing characteristics) are reduced. You can see that they are not combined. Further, Comparative Example 16 has too low strength, and Comparative Example 18 has too low corrosion resistance.
  • the critical significance of each requirement of the present invention is that the aluminum alloy plate of the present invention has both impact absorbability (crushing property), high strength, and corrosion resistance evaluated in the VDA bending test. It is supported.
  • the present invention can provide a 7000 series aluminum alloy plate that is manufactured by conventional rolling and has improved impact absorption (crushing characteristics) at the time of automobile collision without reducing strength. . Therefore, the present invention is suitable for structural members such as automobiles, bicycles, and railway vehicles that contribute to weight reduction.

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Abstract

Dans la présente invention, on fait en sorte qu'une couche de surface d'une plaque d'alliage d'aluminium de la série 7000 fabriquée par un procédé habituel ait une texture dans laquelle l'orientation cubique est favorisée, et que le centre de la plaque ait une texture dans laquelle l'orientation S est favorisée ; c'est-à-dire que la couche de surface de la plaque et le centre de la plaque dans la direction d'épaisseur sont formés pour avoir des textures différentes qui sont les plus appropriées en termes d'absorption d'impact et de résistance, respectivement. Ce faisant, l'absorption d'impact dans une collision de voiture, qui est évaluée par un test de flexion VDA tel que montré sur la figure 1, est améliorée sans diminuer la résistance.
PCT/JP2016/056719 2015-03-04 2016-03-04 Plaque d'alliage d'aluminium WO2016140335A1 (fr)

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EP3532213B1 (fr) 2016-10-27 2021-09-01 Novelis, Inc. Système et procédé permettant de fabriquer des articles en alliage d'aluminium à jauge épaisse
ES2951553T3 (es) 2016-10-27 2023-10-23 Novelis Inc Aleaciones de aluminio de la serie 6XXX de alta resistencia y métodos para fabricar las mismas
WO2019040356A1 (fr) * 2017-08-21 2019-02-28 Novelis Inc. Produits en alliage d'aluminium ayant une microstructure sélectivement recristallisée et procédés de fabrication
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CN107779702A (zh) * 2017-12-06 2018-03-09 中国航发北京航空材料研究院 一种含Ag和Sc的7XXX高强铝合金专用焊丝
EP3556875B1 (fr) * 2018-04-18 2020-12-16 Newfrey LLC Pièce de fixation en alliage d'aluminium contenant du scandium
CN108642348B (zh) * 2018-06-05 2020-06-16 湖南东方钪业股份有限公司 一种Al-Zn-Mg系铝合金型材及其制备方法
CN108456812B (zh) * 2018-06-29 2020-02-18 中南大学 一种低Sc高强高韧高淬透性铝锌镁系合金及制备方法
JP2018204116A (ja) * 2018-08-27 2018-12-27 株式会社神戸製鋼所 アルミニウム合金板
EP3848476A1 (fr) * 2020-01-07 2021-07-14 AMAG rolling GmbH Tôle ou bande en alliage d'aluminium durcissable, pièce de véhicule fabriquée à partir de celle-ci, utilisation et procédé de fabrication de tôle ou de bande
CN114107763B (zh) * 2020-08-26 2023-02-14 宝山钢铁股份有限公司 一种薄带连铸7xxx铝合金薄带及其制备方法
CN112111680A (zh) * 2020-09-17 2020-12-22 湖南恒佳新材料科技有限公司 一种铝合金及其板材的制备方法
CN112522647B (zh) * 2020-11-16 2022-03-18 上海汽车变速器有限公司 含稀土铝硅合金高真空压铸高延伸率热处理方法
CN114438356A (zh) * 2022-01-24 2022-05-06 北京科技大学 一种高强耐蚀高韧Al-Mg-Zn-Ag(-Cu)铝合金的制备方法

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