JP2019094517A - Aluminum alloy material for monolayer heating joint, excellent in deformation resistance - Google Patents

Abstract

To provide an aluminum alloy material having heating joint function as a monolayer, of which reduction of deformation resistance due to processing before blazing is suppressed.SOLUTION: There is provided an aluminum alloy material containing Si:1.5 mass% to 5.0 mass%, Mn of 0.05 mass% to 2.0 mass%, Fe:0.01 mass% to 2.0 mass% and the balance Al with inevitable impurities, and having heating joint function as a monolayer, having a fibrous structure, consisting of a Si-based compound or an AlMnFeSi-based compound, having number density of second phase particles with circle-equivalent diameter of 5.0 μm to 10.0 μm of 1000/mmor less, work hardening exponent n value between 2 points from nominal strain of 0.9 time of nominal strain of maximum load point to nominal strain of the maximum load point of 0.03 or more and local elongation of 1% or more.SELECTED DRAWING: Figure 1

Description

  The present invention relates to an aluminum alloy material for single layer heat bonding and a method of manufacturing the same. More specifically, the present invention relates to a single-layer, heat-bonding aluminum alloy material with improved resistance to deformation at the time of brazing.

  Brazing is often used in methods of manufacturing products such as heat exchangers and heat sinks that are made of aluminum material and have multiple metal joints. As an aluminum material for brazing, a brazing sheet in which a brazing material is clad on a core material made of an aluminum material, and a brazing material have been used. However, the use of a clad material such as a brazing sheet in which a plurality of layers are stacked and joined, and the use of an additional bonding material such as a brazing material are factors that increase the cost of heat exchangers, etc. It had become.

  Therefore, in recent years, an aluminum alloy material that can be heat-bonded in a single layer to the above-described brazing sheet and brazing material has been proposed. (For example, patent document 1). This aluminum alloy material is made of an Al-Si based alloy, and uses the liquid phase generated inside the alloy material by heating for joining. According to this aluminum alloy material, since the above-described liquid phase acts as a brazing material, it can be joined to another member without using a bonding material such as a brazing material while being a single layer. In the present invention, to make bonding possible by heating even without a bonding material in this way is referred to as "heat bonding function". Moreover, joining by the aluminum alloy material which has a heating joining function by such single layer is called "brazing", and the heating temperature at that time is called "brazing temperature" about brazing temperature.

  Since the aluminum alloy material having a heat bonding function in this single layer is in a semi-molten state during brazing, it is important to secure deformation resistance at the brazing temperature. As a method of improving the deformation resistance in this aluminum alloy material, for example, Patent Document 2 proposes that coarsening recrystallized grains during brazing, and heat bonding with a single layer having such an action. Aluminum alloy materials having a function have been clarified.

Patent 5436714 specification Patent 5345264 specification

  However, according to the study of the present inventor, the conventional single layer aluminum alloy material having a heat bonding function may have insufficient deformation resistance at the time of brazing. In particular, in the case of an aluminum alloy material processed at a high degree of processing, a decrease in the deformation resistance of brazing may be observed. In aluminum alloy materials which are members such as heat exchangers and heat sinks, processing such as corrugate molding and press molding is generally performed before brazing. And depending on the form of the member, the increase in the degree of processing can not be avoided. Therefore, for an aluminum alloy material having a single layer heat bonding function, it is necessary to secure deformation resistance at the time of brazing regardless of the presence or absence of processing and the degree of processing.

  The present invention has been made based on the background as described above, and its object is to suppress the decrease in deformation resistance due to processing before brazing for an aluminum alloy material having a single layer heat bonding function. To provide the

  MEANS TO SOLVE THE PROBLEM In order to solve the said subject, this inventor examined the influence of the characteristic on the metallographic structure of the aluminum alloy material which has a heating joining function by a single layer, and processing before brazing.

  The aluminum alloy material having a single layer heat bonding function, which is the subject of the present invention, is made of an Al-Si based alloy containing relatively high concentration of Si. For example, compared to a 3000 series aluminum alloy which is a core material of a general brazing sheet, the Si concentration of the aluminum alloy material having the heat bonding function is high. In the aluminum alloy containing such a high concentration of Si, the density of the second phase particles tends to be high. In an aluminum alloy containing a high concentration of Si, a large amount of crystallized matter is produced in the casting process, and this becomes the above-described second phase particles in the aluminum alloy material. And, it is confirmed that the second phase particles derived from this crystallized material have a relatively large particle size and easily become a recrystallization nucleus. That is, it can be said that an aluminum alloy material having a heat bonding function in a single layer tends to generate recrystallization nuclei at a high density by nature due to its composition.

  Moreover, in the manufacturing process of the aluminum alloy material which has the heat bonding function by the conventional single layer, the material after a casting process is applied to a rolling process and an annealing process. This annealing step is usually performed under conditions that cause recrystallization. For example, in the said patent document 1, the annealing for 2 hours is performed at 380 degreeC in the Example, and this is an annealing process with recrystallization. Moreover, in the said patent document 2, that the annealing process made into a recrystallized structure is provided is clarified (paragraph 0073 of patent document 2). Thus, in the manufacturing process of the aluminum alloy material which has the heat bonding function in the conventional single layer, implementation of the annealing process on the conditions with recrystallization was common.

  Thus, the conventional single-layer aluminum alloy material having a heat bonding function has a high density of the second phase particles derived from the above-mentioned crystallized material in a matrix having a recrystallized structure based on its composition and manufacturing process. It can be said that it has a distributed metallographic structure.

  And, in the aluminum alloy material having a recrystallized structure, during the processing before brazing, the strain tends to be localized around the second phase particles, and the recrystallization nucleus is rapidly increased by the increase of the processing degree It becomes. Therefore, at the time of brazing, refined recrystallized grains are generated, and the crystal grain size is reduced. As grain size is reduced, grain boundary sliding frequently occurs to reduce deformation resistance.

  The inventors of the present invention have considered that in the conventional single-layer aluminum alloy material having a heat bonding function, the deformation resistance at the time of brazing decreases as the degree of processing increases due to the above-described factors. And, in order to alleviate the localization of the recrystallization nuclei due to the processing before brazing described above, it is preferable to make the material structure of the aluminum alloy material into a non-recrystallized fibrous structure without making it a recrystallization structure. Found out.

  According to the inventor of the present invention, in an aluminum alloy material having a fibrous structure, a strain due to processing before brazing is less likely to be localized around the second phase particles, and tends to be dispersed in other parts. Therefore, induction of recrystallized nuclei around the second phase particles can be reduced. Therefore, it is thought that generation | occurrence | production of the fine recrystallization at the time of brazing can be suppressed, and deformation resistance can be maintained by setting it as fibrous structure.

  However, it is difficult to secure the deformation resistance at the time of brazing only by forming a fibrous structure. The fibrous structure is a material structure that itself has a high driving force for recrystallization and is easily recrystallized when it is heated. That is, although the fibrous structure can cope with the problem due to processing before brazing (localization of strain), it can not cope with the problem of recrystallization during brazing (when heating) by itself. That is, in the aluminum alloy material having a heat bonding function as a single layer, which is an object of the present invention, an element for suppressing the refinement of recrystallized grains at the time of heating is further added while adopting a fibrous structure. It is necessary.

  Therefore, as a result of intensive investigations, the inventor of the present invention is required to specify the particle size and number density of particles resulting from the refinement of recrystallized grains for the second phase particles dispersed in the aluminum alloy material. I found it. In addition to this, it was found that the present invention was made to be less susceptible to the degree of processing and to be excellent in deformation resistance at high temperatures by optimizing the predetermined mechanical properties of the aluminum alloy material.

The present invention for achieving the above object is as follows: Si: 1.5% by mass to 5.0% by mass, Mn: 0.05% by mass to 2.0% by mass, Fe: 0.01% by mass to 2.0% by mass An aluminum alloy material containing Al, the balance Al and unavoidable impurities, and having a heat bonding function as a single layer, having a fibrous structure, comprising a Si compound or an AlMnFeSi compound, and having an equivalent circle diameter of 5. The number density of second phase particles of 0 μm to 10.0 μm is 1000 pcs / mm ² or less, and from the nominal strain of 0.9 times the nominal strain of the maximum load point to the nominal strain of the maximum load point An aluminum alloy material having a work hardening index n value of 0.03 or more and a local elongation of 1% or more.

In addition, the present invention is an aluminum alloy material having a heat bonding function with a single layer according to claim 1, which contains one or more of the following elements.
Zn: 0.05 to 6.0%,
Mg: 0.05 to 2.0%
Cu: 0.05 to 1.5%
Ni: 0.05 to 2.0%
Cr: 0.05 to 0.3%
Zr: 0.05 to 0.3%
Ti: 0.05 to 0.3%
V: 0.05 to 0.3%

Moreover, it is also an aluminum alloy material having a heat bonding function in a single layer according to claim 1 or claim 2 containing one or two of the following elements.
In: 0.005 to 0.3%
Sn: 0.005 to 0.3%

Furthermore, the present invention may be an aluminum alloy material having a heat bonding function in a single layer according to any one of claims 1 to 3, which contains one or more of the following elements.
Be: 0.0001 to 0.1%
Sr: 0.0001 to 0.1%
Bi: 0.0001 to 0.1%
Na: 0.0001 to 0.1%
Ca: 0.0001 to 0.05%

  And the manufacturing method of the aluminum alloy material which concerns on this invention is a casting process which manufactures a slab by DC casting, and the heating process before hot-rolling without performing a homogenization process process or a homogenization process after the said casting process. Heating after performing any of the following heating steps, the step of cold rolling after the hot rolling step, and at least one annealing step performed during the cold rolling step The casting speed of the casting step is 20 to 100 mm / min, and the conditions of the heating step before the homogenization treatment step or hot rolling are a heating temperature of 350 ° C. to 480 ° C., and a holding time of 0 to 30 hours. In the method of manufacturing an aluminum alloy material, annealing is performed at a temperature and a time that do not cause recrystallization in the annealing step.

  In the method for producing an aluminum alloy material according to the present invention, a casting step of producing a plate-like ingot by continuous casting, a homogenization treatment step performed after the casting step, and cold rolling after the homogenization treatment step And at least one annealing step performed during the cold rolling step, wherein the casting speed of the casting step is 500 to 3000 mm / min, and the condition of the homogenization treatment step is a heating temperature of 350 ° C. The method for producing an aluminum alloy material may be a temperature of -480 ° C., a holding time of 1 to 10 hours, and annealing at a temperature and a time that do not cause recrystallization in the annealing step.

  The above two manufacturing methods include the case where cold rolling is performed after the annealing step, and the working ratio in the cold step is preferably 20% or less.

  The aluminum alloy material according to the present invention has a heat bonding function in a single layer, and has a small decrease in deformation resistance due to processing before brazing. According to the present invention, it is expected to improve the product size and yield of heat exchangers and the like. Moreover, even if processing stronger than before is performed before brazing, it is possible to maintain the deformation resistance during brazing.

While showing an example of the crystal grain structure of the aluminum alloy material manufactured by the Example and the comparative example, it is a figure explaining the method when judging the fibrous structure visually.

  Hereinafter, the aluminum alloy material for single-layer heat bonding according to the present invention and the method for producing the same will be described in more detail. First, constituent elements, material structures, and mechanical properties of the aluminum alloy material according to the present invention will be described. In the specification of the present application, when simply expressed as "%" in the description of the composition of the alloy, "mass%" is meant.

I. Constituent Elements of Aluminum Alloy Material of the Present Invention (1) Essential Elements The aluminum alloy material of the present invention contains Si, Mn and Fe as essential elements. The technical significance and addition amounts of these essential elements are as follows. The aluminum alloy material according to the present invention is composed of aluminum and unavoidable impurities as the balance other than the following essential elements and optional additional elements.

・ Si
Si is an element that forms a liquid phase of an Al-Si system and contributes to bonding. However, when the Si concentration is less than 1.5%, a sufficient amount of liquid phase can not be generated, so that the liquid phase bleeds out less, and the bonding becomes incomplete. On the other hand, if it exceeds 5.0%, the amount of Si particles in the aluminum alloy material increases and the amount of liquid phase generation increases, so the material strength during heating extremely decreases and it is difficult to maintain the shape as a fin material Become. Therefore, the Si concentration is defined as 1.5% to 5.0%. The Si concentration is preferably 1.6% to 3.5%, more preferably 2.0% to 3.0%. The amount of the liquid phase that exudes increases as the plate thickness increases and the heating temperature increases, so the amount of liquid phase required at the time of heating may be necessary depending on the structure and dimensions of the fins of the heat exchanger to be manufactured. It is desirable to adjust the amount of Si and the brazing temperature to be

・ Mn
Mn acts as a dispersion strengthening by forming an AlMnFeSi-based intermetallic compound which is a second phase particle together with Si and Fe. Mn also forms a solid solution in the aluminum matrix and acts as a solid solution strengthening. Thus, Mn is an important additive element that improves the strength of the alloy material. When the Mn content exceeds 2.00%, coarse intermetallic compounds are easily formed to lower the corrosion resistance. On the other hand, when the Mn content is less than 0.05%, the above effect is insufficient. Therefore, the Mn content is set to 0.05 to 2.00%. The Mn content is preferably 0.10 to 1.50%.

・ Fe
In addition to having the effect of improving the strength by forming a solid solution in the matrix slightly, Fe is dispersed as AlMnFeSi-based crystallized matter or precipitate and has an effect of preventing strength reduction particularly at high temperature. When the content of Fe is less than 0.01%, not only the above effects can not be sufficiently obtained, but also it is necessary to use a high purity metal, which leads to an increase in material cost. On the other hand, if the Fe content exceeds 2.00%, a coarse intermetallic compound is formed during casting, which causes problems in manufacturability. In addition, when the bonded body is exposed to a corrosive environment (in particular, a corrosive environment in which a corrosive liquid flows), the corrosion resistance is lowered. Furthermore, since the crystal grains recrystallized by heating at the time of bonding are refined and the grain boundary density is increased, the amount of deformation during bonding is increased and the dimensional change before and after bonding is increased. Therefore, the Fe content is 0.01 to 2.00%. The content of Fe is preferably 0.10% to 0.60%.

(2) Selectively Added Elements The aluminum alloy material according to the present invention can selectively contain Mg, Cu, Ni, Cr, Zr, Ti, V, Be, Sr, Bi, Na, Ca in addition to the above-described essential elements. And Zn, In and Sn can be contained alone or in combination of two or more.

・ Mg
Mg becomes Mg ₂ Si after brazing to cause age hardening and improve strength. Therefore, Mg is an additive element that exerts the effect of strength improvement. If the amount of Mg added exceeds 2.0%, it reacts with the flux to form a high melting point compound, and the bonding property is significantly reduced. Therefore, the amount of Mg added is preferably 2.0% or less. The preferable addition amount of Mg is 0.05% to 2.0%. In the present invention, not only Mg but also other alloy components, 0% or less is included in the case of a predetermined addition amount or less.

・ Cu
Cu is an additive element which is dissolved in the matrix to improve strength. However, when the amount of added Cu exceeds 1.5%, the corrosion resistance is lowered. Therefore, the addition amount of Cu is preferably 1.5% or less. The preferable addition amount of Cu is 0.05% to 1.5%.

・ Ni
Ni crystallizes or precipitates as an intermetallic compound, and has the effect of improving the strength after bonding by dispersion strengthening. The amount of Ni added is preferably 2.0% or less. The preferred addition amount is 0.05% to 2.0%. When the content of Ni exceeds 2.0%, coarse intermetallic compounds are easily formed, and the processability is reduced. In addition, self-corrosion also decreases.

・ Cr
Cr improves strength by solid solution strengthening, and an Al-Cr based intermetallic compound precipitates to act on coarsening of crystal grains after heating. When the addition amount exceeds 0.3%, coarse intermetallic compounds are easily formed, and the plastic formability is reduced. Therefore, the addition amount of Cr is preferably 0.3% or less. A more preferable addition amount is 0.05% to 0.3%.

・ Zr
Zr precipitates as an Al—Zr intermetallic compound and exhibits the effect of improving the strength after bonding by dispersion strengthening. In addition, Al-Zr-based intermetallic compounds act to coarsen grains during heating. When the addition amount exceeds 0.3%, coarse intermetallic compounds are easily formed, and the plastic formability is reduced. Therefore, the addition amount of Zr is preferably 0.3%. The preferred addition amount is 0.05% to 0.3%.

・ Ti, V
Ti and V are dissolved in the matrix to improve strength, and are also distributed in layers and have the effect of preventing the progress of corrosion in the thickness direction. When the amount of addition exceeds 0.3%, a huge crystallized product is generated, which impairs the formability and the corrosion resistance. Therefore, the addition amounts of Ti and V are each preferably 0.3% or less. A more preferable addition amount is 0.05% to 0.3%.

・ Zn
Zn is an element effective for improving the corrosion resistance by the sacrificial corrosion protection action. Zn has the effect of dissolving in a matrix almost uniformly and causing natural potential to grow. For example, by using the aluminum alloy material according to the present invention as a fin material and causing it to age, it is possible to exhibit a sacrificial anticorrosive action that relatively suppresses the corrosion of the joined tubes. If the Zn content is less than 0.05%, the effect of potential hatching is insufficient. On the other hand, when the Zn content exceeds 6.00%, the corrosion rate is increased, the self corrosion resistance is reduced, and the sacrificial corrosion protection action is also reduced. Therefore, the Zn content is set to 0.05 to 6.00%. The Zn content is preferably 0.10% to 5.00%.

・ Sn, In
Sn and In have an effect of exhibiting a sacrificial anode action. When the addition amount exceeds 0.3%, the corrosion rate becomes fast and the self corrosion resistance is lowered. Therefore, the addition amount of each of these elements is preferably 0.3% or less. A more preferable addition amount is 0.05% to 0.3%.

・ Be, Sr, Bi, Na, Ca
Be, Sr, Bi, Na, and Ca further improve the bondability by improving the characteristics of the liquid phase. The preferable range of each of these elements is Be: 0.0001% to 0.1%, Sr: 0.0001% to 0.1%, Bi: 0.0001% to 0.1%, Na: 0.0001% 0.1%, Ca: 0.0001% to 0.05%, and one or more of these may be added as needed. These trace elements can improve bondability by finely dispersing Si particles, improving the fluidity of the liquid phase, and the like. If these trace elements are less than the above-mentioned more preferable specified range, their effects are small, and if they exceed the above more preferable specified range, adverse effects such as corrosion resistance may be caused. In the case where one or more of Be, Sr, Bi, Na and Ca are added, it is necessary that all of the respective additive components be within the above-mentioned preferable or more preferable component range.

II. Metallographic Structure of Aluminum Alloy Material According to the Present Invention As described above, the aluminum alloy material having a heat bonding function with a single layer according to the present invention is characterized by its metallographic structure, and has a fibrous crystal grain structure (hereinafter referred to as fiber And further limit the density of second phase particles in a predetermined size range. The technical significance of these will be described below.

(A) Fibrous structure The aluminum alloy material for single layer heat bonding according to the present invention is characterized by having a fibrous structure. By forming into a fibrous structure, distortion due to processing before brazing can be uniformly dispersed without being localized around the second phase particles. And thereby, the increase in the recrystallization nucleus at the time of processing is suppressed, and the fall of the deformation resistance by fine recrystallization at the time of brazing is suppressed. Here, the fibrous structure is a metal structure composed of crystal grains elongated in the rolling direction. Specifically, in the present invention, the metal structure has crystal grains having an aspect ratio of 10 or more.

In the case of measuring the aspect ratio of crystal grains for determination of the fibrous structure, crystal grains are observed by anodic oxidation on the cross section perpendicular to the width direction of the aluminum alloy material, and It is preferred to measure the shape. As the conditions of the anodic oxidation method, for example, a 3.3% HBF ₄ aqueous solution is used, and a current is flowed at a voltage of 30 V for 60 seconds to generate an oxide film. The sample after anodic oxidation can be observed with an optical microscope using a polarizing filter. The observation magnification at this time is not particularly limited, but is selected about 50 to 200 times depending on the size of the crystal grain.

  When determining the aspect ratio of crystal grains for determination of fibrous structure, it is preferable to observe at least five fields of view for one sample. At this time, it is preferable to analyze an image including an alloy material having a length of at least 300 μm or more as one view. It is preferable to prepare and measure an image for at least five fields of view. In image analysis, the aspect ratio of crystal grains is determined from an image captured by an optical microscope.

  Then, it is possible to determine the success or failure of the fibrous tissue by image analysis of the image taken with a microscope or direct measurement of the image. The image analysis can use appropriate software, and the analysis calculates the average aspect ratio. When the average aspect ratio is calculated to be 10 or more, it is determined that the visual field has a fibrous structure. When it is determined to be a fibrous tissue in 80% or more of the number of fields of view with respect to the number of fields of observation, the sample is made of an alloy material of a fibrous tissue. When an image is directly measured, when ten or more crystal grains with an aspect ratio of 10 or more can be measured per one visual field, it is determined that the visual field has a fibrous structure. When it is determined to be a fibrous tissue in 80% or more of the number of fields of view with respect to the number of fields of observation, the sample is made of an alloy material of a fibrous tissue.

(B) Number density of second phase particles of circle equivalent diameter 5 μm to 10 μm The aluminum alloy material for single layer heating bonding according to the present invention includes second phase particles composed of a Si based compound or an AlMnFeSi based compound. And, in the present invention, the second phase particle density of circle equivalent diameter of 5 μm to 10 μm is made to be 1000 / mm ² or less. The second phase particles are particles of a phase different from that of the matrix Al or Al alloy. The second phase particles are composed of a Si-based compound or an AlMnFeSi-based compound. Specifically, the Si-based compounds are single Si and Si compounds. The Si compound is a compound containing Si, and for example, there is a compound containing an element such as Ca, P or the like in a part of single Si. The AlMnFeSi-based compound is an intermetallic compound produced from Al and an additive element of the alloy. Specifically, they are Al-Fe based compounds, Al-Fe-Si based compounds, Al-Mn-Si based compounds, Al-Fe-Mn based compounds, Al-Mn-Fe-Si based compounds and the like.

  The second phase particles of the present invention are derived from the crystallized matter or precipitate formed in the production process of the aluminum alloy material. Crystallized products are mainly generated from the liquid phase in the casting process, and precipitates are mainly generated from the solid phase in the processes after the casting process such as homogenization treatment. However, in the present invention, it does not matter whether the second phase particles observed when observing the metal structure of the aluminum alloy material are caused by the crystallized matter or the precipitate. Regardless of the origin of the second phase particles, if they fall within a specific particle size range, the second phase particles defined in the present invention are obtained. The meanings of the terms "crystallized" and "precipitate" in the present specification are distinguished based only on the timing of their formation. Both are synonymous in that they become "second phase particles" in the aluminum alloy material.

  In the present invention, the reason for limiting the density of the second phase particles in the specific particle size range is to suppress the progress of recrystallization during brazing of the aluminum alloy material. That is, as described above, the aluminum alloy material of the present invention is characterized by having a fibrous structure. While this fibrous structure has the effect of uniformly dispersing the strain and suppressing recrystallization nucleation at the time of processing before brazing, at the time of brazing (at the time of heating), a conventional aluminum alloy material and It is a material structure with a high driving force for recrystallization in comparison. Therefore, in the present invention, the density of the second phase particles that can be recrystallization nuclei at the time of brazing is regulated, and the influence thereof is reduced. This is to suppress recrystallization that occurs at the time of brazing.

And, the second phase particles that may become recrystallized nuclei at the time of brazing are second phase particles having a circle equivalent diameter of 5 μm to 10 μm and a relatively large particle size. According to the inventors of the present invention, when the number density (area density) of second phase particles having a circle equivalent diameter of 5 μm to 10 μm exceeds 1000 pieces / mm ² , recrystallized grains become finer, and the deformation resistance decreases. Therefore, the density of such second phase particles is defined as 1000 particles / mm ² or less. The number density of the second phase particles having a circle equivalent diameter of 5 μm to 10 μm is preferably low in order to suppress the refinement of recrystallized grains at the time of brazing, and the one without such second phase particles is preferable.

  In the present invention, it is not necessary to specify the presence or absence and the number density of second phase particles having an equivalent circle diameter of less than 5 μm. According to a study by the present inventors, fine second phase particles having a circle equivalent diameter of less than 5 μm are less likely to be recrystallization nuclei. In addition, it is not necessary to particularly define second phase particles having a circle equivalent diameter of more than 10 μm. It is because such coarse second phase particles are hardly present under the preferable production conditions of the aluminum alloy material of the present invention described later.

  In the present invention, the equivalent circle diameter of the second phase particles is the meaning of the equivalent circle diameter. The equivalent circle diameter of the second phase particles can be measured by performing SEM observation on an arbitrary cross section of the aluminum alloy material. The equivalent circle diameter of the second phase particles can be determined by image analysis of the SEM image obtained by the SEM observation. The second phase particles composed of Si and the second phase particles composed of an AlMnFeSi-based compound can be distinguished by the contrast density in the SEM image. The exact composition can be confirmed by EPMA (electron beam microprobe analysis).

III. Mechanical Properties of Aluminum Alloy Material According to the Present Invention The aluminum alloy material for single-layer heat bonding according to the present invention has the above-described features in composition and material structure. And it originates in them and the aluminum alloy material for single layer heating joining which concerns on this invention shows the characteristic tendency in n value and local elongation.

(A) n value (work hardening index)
In the aluminum alloy material for single layer heat bonding according to the present invention, an n value between two points from a nominal strain of 0.9 times the nominal strain at the maximum load point to a nominal strain at the maximum load point is 0.03. And above. Here, the n value is called a work hardening index, and is an index indicating the ease of work hardening when the material is deformed. The n value can be determined from the true stress and true strain obtained based on the nominal stress-nominal strain curve obtained from the tensile test. The value of n varies depending on the range of nominal distortion applied during calculation. The n value in the range from a nominal strain a times the nominal strain at the maximum load point to a nominal strain b times the maximum load point can be determined using the following equation (1).

  The nominal strain range for the n value specification of the aluminum alloy material according to the present invention (equations (1) a and b) is the nominal strain of 0.9 times the nominal strain of the public maximum load point to the nominal of the maximum load point. It is considered as distortion (a = 0.9, b = 1.0). Generally, in an aluminum alloy, the n value tends to be high in a region where the nominal strain is low, and the n value tends to be low in a region where the nominal strain is high. In the aluminum alloy material according to the present invention, it is important to maintain a high n value even in a region close to the maximum load point where the nominal strain is high and not to localize the strain due to processing. Therefore, it was decided to apply the n value between two points of the nominal strain (1.0 times) of the maximum load point from the nominal strain of 0.9 times the nominal strain of the maximum load point.

  In the present invention, the n value in the range from a nominal strain of 0.9 times the nominal strain at the maximum load point to the nominal strain at the maximum load point is set to 0.03 or more. The n value, which is a work hardening index, is an index showing the ease of work hardening, and as the material which is easy to work harden is deformed more uniformly, it can be uniformly deformed. If the n value is less than 0.03, deformation is locally introduced when a distortion smaller than the nominal strain at the maximum load point is applied during processing before brazing. Therefore, the recrystallized grain size at the time of brazing becomes finer, and the deformation resistance decreases. For this reason, the n value is made 0.03 or more. The preferable value of this n value is 0.04 or more, and a further preferable value is 0.05 or more. Although there is no upper limit of n value, it is preferable to make it substantially 0.98 or less.

(B) Local Elongation In the aluminum alloy material for single-layer heat bonding according to the present invention, the local elongation is set to 1% or more. The local elongation is the difference between the strain at the point of maximum load and the strain at break of the nominal stress-strain curve obtained from the tensile test. If the local elongation is less than 1%, deformation is locally introduced when a strain larger than the strain at the maximum load point is applied during processing before brazing. Therefore, there is a possibility that the recrystallized grain at the time of brazing becomes fine and the deformation resistance is lowered. The preferable value of this local elongation is 2% or more, and more preferable is 4% or more. The upper limit of the local elongation should not be limited, but is preferably substantially 30%.

IV. Method of Producing Aluminum Alloy Material According to the Present Invention Next, a method of producing an aluminum alloy material for single-layer heat bonding according to the present invention will be described. The aluminum alloy material of the present invention can basically be manufactured according to a conventional method, but special attention must be paid to the heating conditions after casting. As described above, in the present invention, it is necessary to have a fibrous structure which is a non-recrystallized structure. Hereinafter, as a method of manufacturing an aluminum alloy material of the present invention, a case of DC casting and a case of continuous casting (CC) will be described.
(A) Production Method by DC Casting A slab cast by a DC casting method becomes the aluminum alloy material of the present invention through a heating step before hot rolling, a hot rolling step, a cold rolling step, and an annealing step. Here, in the casting step, although a crystallized product can be produced, the casting speed is 20 to 100 mm / in order to suppress the formation of second phase particles having an equivalent circle diameter of 5 μm to 10 μm which becomes a recrystallization nucleus at brazing. It is preferable to use a minute. In addition, you may give a homogenization process before hot rolling.

  The slab produced by the DC casting method can be subjected to a heating step prior to hot rolling after the homogenization treatment or without the homogenization treatment. As for the conditions of this homogenization process and a heating process, it is desirable to set heating holding temperature to 350-480 degreeC, respectively, and to make holding time into the range of 0 to 30 hours. If the holding temperature is less than 350 ° C., the deformation resistance of the slab in hot rolling may be large and cracking may occur. On the other hand, in this homogenization treatment and heating step, fine precipitates may be generated, and heat treatment at high temperature for a long time causes coarsening of second phase particles. When the holding temperature exceeds 480 ° C., or when the holding time exceeds 30 hours, coarsening of the second phase particles occurs, and the second phase particle density with a circle equivalent diameter of 5 μm to 10 μm increases. Further, in the heat treatment at high temperature for a long time, the solid solution amount of the additive element increases, and the recrystallized grains after brazing are refined. In addition, holding time 0 time means ending heating immediately after reaching above-mentioned heating holding temperature.

  And it hot-rolls after the said heating process, and according to the content of refining, it is applied to the cold-working process and the annealing process. In the case of the H1 n temper, the hot rolled material is subjected to a cold rolling process after the hot rolling process is completed. The conditions of the cold rolling process are not particularly limited. Then, in the middle of the cold rolling process, an annealing process for annealing the cold rolled material is provided at least once. The conditions of this annealing process are implemented on the conditions which recrystallization does not produce. Specifically, the material is heated at 150 to 300 ° C. for 1 to 5 hours. If the temperature is less than 150 ° C., the material is not sufficiently softened, the processability is reduced, and the elongation at the final thickness is reduced. If it exceeds 300 ° C., recrystallization tends to occur. Even if the temperature is 300 ° C. or less, recrystallization may occur depending on the alloy composition and the manufacturing process. In this case, the temperature is set such that recrystallization does not occur within the above temperature range.

  After the annealing step, the cold-rolled material is subjected to final cold rolling to obtain a final thickness. If the processing ratio in this final cold rolling (processing ratio = (plate thickness before processing-plate thickness after processing) / plate thickness% before processing) is too high, the driving force for recrystallization during brazing is large. Because the crystal grains become smaller, deformation during brazing becomes larger. The final cold rolling is optional and may not necessarily be performed, and the plate thickness after the annealing step may be the final plate thickness. Moreover, it is preferable to set the processing rate in the case of performing final cold rolling to about 3 to 20%.

  In the case of producing an aluminum alloy material by H2n tempering, after the completion of the hot rolling process, the hot rolled material is processed to the final thickness in the cold rolling process and then the annealing process (final annealing) is performed; As in the case of the H1 n temper, at least one annealing process may be provided in the middle of the cold rolling process, and the final annealing may be performed after the final cold rolling. In any case, the annealing step is carried out under the condition that recrystallization does not occur as described above.

(B) Manufacturing method by continuous casting As a continuous casting method, it is particularly limited as long as it is a method of continuously casting a plate-like ingot, such as a twin roll continuous casting rolling method or a double belt continuous casting method. Absent. The twin roll type continuous casting and rolling method is a method in which molten aluminum is supplied between a pair of water cooling rolls from a hot water supply nozzle made of a refractory to continuously cast and roll a thin plate, and the hunter method, 3C method and the like are known. ing. Further, in the double-belt type continuous casting method, molten metal is poured between rotating belts facing each other vertically and water-cooled, and the molten metal is solidified by cooling from the belt surface to form a slab; It is a continuous casting method in which a slab is continuously drawn out and wound in a coil shape, and the Hazley method and the like are known.

  In the casting process of the plate-like ingot by the continuous casting method as described above, the casting speed is 500 to 3000 mm in order to suppress the formation of second phase particles having an equivalent circle diameter of 5 μm to 10 μm which becomes a recrystallization nucleus at brazing. It is necessary to make it / min.

  The plate-like ingot cast by the continuous casting method is subjected to homogenization treatment in that state. Then, an annealing process is performed in the process of cold-rolling to final plate thickness. This annealing step needs to be performed at least once or more.

  The homogenization treatment is preferably performed at 350 to 480 ° C. for 1 to 10 hours in order to precipitate fine precipitates and obtain an appropriate metallographic structure. If it is less than 350 ° C., the precipitation of fine precipitates becomes insufficient. On the other hand, the fine precipitates generated here can also be distributed in the aluminum alloy material as second phase particles. When the homogenization treatment temperature exceeds 480 ° C., the second phase particles become coarse, and the density of second phase particles having an equivalent circle diameter of 5 μm to 10 μm increases. Moreover, the said effect is not enough in the homogenization time less than 1 hour, and it becomes economically disadvantageous in the said homogenization time exceeding 10 hours, since the said effect is saturated.

  In the annealing step, the material is softened to make it easier to obtain the desired material strength in the final rolling. It is necessary to carry out the annealing process under the condition that recrystallization does not occur. Specifically, it is carried out at 150 to 300 ° C. for 1 to 5 hours. If the temperature is less than 150 ° C., the material is not sufficiently softened, so that the processability is reduced and the elongation at the final thickness is reduced. If it exceeds 300 ° C., recrystallization tends to occur. Even if the temperature is 300 ° C. or less, recrystallization may occur depending on the alloy composition and the manufacturing process. In this case, the temperature is set such that recrystallization does not occur within the above temperature range.

  After the annealing step, the rolled material is subjected to final cold rolling to obtain an aluminum alloy material of final thickness. In the case of the H1 n temper, if the working ratio at the final cold rolling step is too large, the recrystallization driving force during brazing becomes large and the crystal grains become small, so the deformation resistance during brazing decreases. . The final cold rolling is optional and may not necessarily be performed, and the plate thickness after the annealing step may be the final plate thickness. Moreover, it is preferable to set the processing rate in the case of performing final cold rolling to about 3 to 20%.

  In the case of producing an aluminum alloy material by H2n tempering, after the completion of the hot rolling process, the hot rolled material is processed to the final thickness in the cold rolling process and then the annealing process (final annealing) is performed; As in the case of the H1 n temper, at least one annealing process may be provided in the middle of the cold rolling process, and the final annealing may be performed after the final cold rolling. In any case, the annealing step is carried out under the condition that recrystallization does not occur as described above.

Hereinafter, the present invention will be described in comparison with comparative examples by examples.
In the present example, the aluminum alloys shown in Tables 1 to 4 were melted and DC cast, and then the hot rolling process and the cold rolling process were performed. In the middle of the cold rolling process, intermediate annealing was performed under conditions that do not recrystallize, and final cold rolling was performed to obtain an aluminum alloy material having a final plate thickness of 0.1 mm. In this example, in the heating step before hot rolling, the temperature was raised to 450 ° C. and held at that temperature for 10 hours. Moreover, the annealing process in the middle of the cold rolling process was maintained at 200 ° C. for 3 hours to prevent recrystallization. Furthermore, the final cold rolling rate was 10%.

  However, alloy A69 of Table 4 made the final cold-rolling rate 20%. Moreover, in alloy A70 of Table 4, the hot rolling temperature was 420 ° C. Moreover, in order to set it as H2 n temper at alloy A71 of Table 4, the plate thickness was made into 0.1 mm by cold rolling after hot rolling, and the final annealing after that was performed to make a test material. The final annealing was held at 200 ° C. for 3 hours.

  Further, in the alloy A72 of Table 4, a plate-like ingot was manufactured by melting and continuously casting the same aluminum alloy as the alloy A1 of Table 1. After the plate-like ingot is homogenized and cold-rolled, an annealing step (intermediate annealing) is carried out under conditions where recrystallization does not occur, and final cold-rolling is carried out. It was an aluminum alloy material of 1 mm. The homogenization treatment was heated to 450 ° C. and held at that temperature for 10 hours. The intermediate annealing was held at 200 ° C. for 3 hours. In addition, the final cold rolling ratio was 10%.

Comparative example

  The aluminum alloy shown in Table 5 was melted and DC-cast in the same manner as in the example, and then a hot rolling step and a cold rolling step were performed. In this comparative example, alloys B1 to B5 in Table 5 were produced under the same conditions as the example (heating step before hot rolling, annealing step), and in the alloys B6 to B10, manufacturing conditions different from the example were applied. . Specifically, in the alloy B6, the annealing temperature is set to 350 ° C. for 3 hours. In the alloy B7, the H2n temper was used, the intermediate annealing process was not performed, and the final annealing process was performed at an annealing temperature of 350 ° C. for 3 hours. In the alloy B8, the heating temperature in the heating step before hot rolling was set to 520 ° C., and the holding time was set to 5 hours. In the alloy B9, the heating temperature before hot rolling was 350 ° C. In the alloy B10, the final cold rolling reduction rate is 30%.

  With respect to the aluminum alloy materials of the above Examples and Comparative Examples, determination of grain structure (fibrous structure) as observation of metal structure, measurement of number density of second phase particles, and mechanical characteristics (n value, local area) Physical properties were measured.

  The crystal grain structure of various manufactured plate materials (base plates) was determined by observing a cross section perpendicular to the width direction with an optical microscope. In the observation, after the test material was filled with resin and polished, the surface was treated by anodic oxidation to make it easy to observe the grain structure. In the present embodiment and the comparative example, the crystal grain structure of the sample of the present invention is photographed in five fields of view with each sample using an optical microscope, and commercially available image analysis software (trade name: A Image Kun, manufactured by Asahi Kasei Corporation) Image analysis was performed to measure the average aspect ratio of the crystal grains. The grain structure having an average aspect ratio of 10 or more was determined to be a fibrous structure, and the one having an average aspect ratio of less than 10 was determined to be a recrystallized structure. Then, when it was determined that the fibrous structure was obtained in 80% of the 5 views (4 views), the grain structure of the sample was determined to be an alloy material of a fibrous structure, and the rest was determined to be an alloy material of a recrystallized structure. .

  Moreover, depending on a test material, the crystal grain was observed in linear form, and there existed some to which measurement of the aspect ratio by image analysis is difficult. For such test materials, the fibrous structure was judged based on direct measurement by visual judgment using a crystal grain sample of aspect ratio 10.

  An example of the grain structure determination method by visual observation will be described. FIG. 1 shows an example of a fibrous structure observed in the aluminum alloy sheet material of this example and an enlarged image thereof. In FIG. 1, the white contrast crystal grains do not necessarily have a constant thickness. This is due to the influence of adjacent crystal grains.

  Such crystal grain structure was determined by drawing a rectangle having an aspect ratio of 10, with the thickness being the short side, with the thickness of the thickest crystal grain as a reference among the observed crystal grains. Specifically, a rectangular figure having an aspect ratio of 10 as shown in the enlarged image on the lower side of FIG. 1 was created and judged. In the example of the enlarged image of FIG. 1, the crystal grain to be measured is determined to have an aspect ratio of 10 or more because the crystal grain to be measured is longer than a rectangular parallelepiped having an aspect ratio of 10. Here, crystal grains of white contrast in the enlarged image of FIG. 1 are appropriately selected, and rectangular figures having a length such that the aspect ratio is 10 as described above are created and compared, and the aspect ratio is 10 or more It was judged. When the number of crystal grains having an aspect ratio of 10 or more was 10 or more per one visual field, a fibrous structure was formed. When the fibrous structure was determined in 80% of the 5 views (4 views), the grain structure of the sample was determined to be an alloy material of a fibrous structure, and the rest was determined to be an alloy material of a recrystallized structure.

  In the determination of the crystal grain structure by visual observation of the image, the second phase particles may be observed to be large by the anodic oxidation method, and there may be a part where observation of the crystal grains is difficult. Therefore, it is difficult to accurately measure the exact aspect ratio of the crystal grains in a sample in which a large number of second phase particles are generated. In particular, crystal grains observed with a near black contrast in polarization observation are difficult to distinguish from the second phase. From such a reason, it is preferable to measure an aspect ratio for crystal grains observed with white contrast in crystal grain structure observation.

  Next, the number density (area density) of second phase particles having an equivalent circle diameter of 5 μm to 10 μm was measured for each aluminum alloy plate material (base plate). This measurement was performed by SEM observation (reflected electron image observation) of a cross section perpendicular to the thickness direction. The observation was performed for each of five test fields for each test material, and the surface density of the second phase particles having a circle equivalent diameter exceeding 5 μm was examined by image analysis of SEM photographs (magnification of 1000 times) of each field of view.

  The n value and the local elongation of each aluminum alloy sheet (base plate) were measured. The measurement of these physical property values was carried out by forming and processing a fin material (dimension: width 35 mm × length 200 mm) cut into a strip shape, performing a tensile test at normal temperature, and based on the result. The n value is based on the nominal stress-nominal strain curve obtained from the tensile test to create a true stress-true strain, and according to the equation (1) described above, a nominal strain of 0.9 times the nominal strain at the maximum load point From this, the n value between the two points of the nominal strain at the maximum load point was determined. The local elongation was determined from the nominal stress-nominal strain line obtained from the tensile test. In this measurement test, the breaking strain was taken as the nominal strain at the maximum load point for those broken without showing the maximum load point.

  After conducting the above metal structure evaluation and physical property value measurement, an evaluation test was performed on each aluminum alloy plate material (base plate). This evaluation test was performed on evaluation of deformation resistance by processing and evaluation of brazing property.

[Evaluation of deformation resistance by processing]
In the evaluation test of deformability, 10% of cold working was added to the aluminum alloy sheet to simulate the process before brazing. Then, it cut | disconnected to the test piece for sag test of width 16 mm and protrusion length 50 mm, and conducted the sag test on the conditions of 600 degreeC x 3 min. As a result of the sag test, those having a drooping amount of 20 mm or less are "◎", those exceeding 20 mm but 30 mm or less are "○", those exceeding 30 mm are 40 mm or less "」 ", those exceeding 40 mm are" X. In the present example, the results of “Δ” or more were determined to have good pair deformability.

[Evaluation of solderability]
In the evaluation test of brazing property, the manufactured aluminum alloy sheet was cut into a strip of 20 mm in width and 300 mm in length and subjected to corrugate processing. Assemble the corrugated fin material in a mini core shape by combining it with the extruded flat tube of JIS A1050, spray the fluoride core flux on the mini core and dry it, and then hold it at a temperature of 600 ° C for 3 minutes in a nitrogen atmosphere. Bonding was performed. The cross section of the mini core after brazing was observed, and the presence or absence of the fillet at the joint between the fin and the tube was examined to evaluate the brazeability. At that time, the formation of fillet is 100%, "「 ", less than 100%, 98% or more," ○ ", 90% or more and less than 98%," Δ ", less than 90% The thing was made into "x". In this example, the result of “Δ” or more was determined to be good in the brazeability. In addition, in this evaluation test of brazing property, only alloys A24 to A26 were evaluated by brazing in vacuum without applying a flux.

  Moreover, in the aluminum alloy board material in a present Example and a comparative example, evaluation of manufacturability in board material manufacture was performed beforehand. The evaluation of manufacturability can not be performed because the load exceeded the equipment capacity during the hot rolling process and therefore the production of the plate is not possible or because the crack occurs during the cold rolling process. The case where it became was judged as "x". When the plate material could be manufactured, it was judged as "o."

  Tables 6 to 10 show the measurement results and the evaluation results of the aluminum alloy sheet materials of the present example and the comparative example. From these tables, the following examination results were obtained regarding the configuration and effects of the present invention.

From Tables 6 to 9, in all the aluminum alloy materials of Examples 1 to 72 having various conditions specified in the present invention, the grain structure exhibits a fibrous structure, and the circle equivalent diameter is 5 μm to 10 μm. The number density (area density) of the second phase particles, the n value, and the local elongation all satisfy the conditions.
And these examples were favorable in the deformation resistance after processing. Moreover, there was no problem in manufacturability and the brazing property was also good.

  On the other hand, according to Table 10, in Comparative Example 1 to Comparative Example 10 (Alloys B1 to B10), the composition or the metal structure and the physical property value (n value) attributed to the manufacturing conditions were out of the definition of the present invention . As a result, there was a point which is inferior in evaluation of deformation resistance, and brazability. Specifically, it is as follows.

In Comparative Example 1, since the amount of Si was too small, the flowing solder ran short and the brazing property became x.
In Comparative Example 2, since the amount of Si is too large, melting and erosion of the core material become remarkable, and the deformation resistance after processing becomes x.
In Comparative Example 3, since Mn was too small, coarsening of crystal grains after brazing was insufficient, and the deformation resistance after processing became x.
In Comparative Example 4, since Mn was too large, coarse intermetallic compounds were formed during casting, which made rolling difficult and the productivity became x.
In Comparative Example 5, since there was too much Fe, a coarse intermetallic compound was formed during casting, which made rolling difficult and the productivity became x.
As described above, in Comparative Examples 1 to 5, the characteristics were insufficient due to the composition.

Moreover, in the comparative example 6, the temperature of the annealing process (intermediate annealing) was high. Therefore, the grain structure was not a fibrous structure but a recrystallized structure. As a result, the deformation resistance after processing was x. Also, this alloy had a low local elongation of less than 1%.
The alloy of Comparative Example 7 also has a high temperature in the annealing step. In this comparative example, although the annealing temperature is the final annealing temperature, the annealing temperature is high and has a recrystallized structure, and the deformation resistance after processing is x. This alloy also had low local elongation.
From these comparative examples, when the temperature of the annealing process is high and recrystallization occurs, the grain structure of the alloy material changes from a fibrous structure (not recrystallized) to a recrystallized structure, and the deformation resistance after processing is reduced. That was confirmed.

In Comparative Example 8, the heating temperature in the heating step before hot rolling was high, and the number density (surface density) of second phase particles having a circle equivalent diameter of 5 μm to 10 μm exceeded the preferable range. Due to the excessive formation of coarse second phase particles, recrystallized grains are refined at the time of brazing, and the deformation resistance after processing is x.
Considering the results of Comparative Example 8 and the results of Comparative Examples 6 and 7 above, in the aluminum alloy material having a heat bonding function in a single layer, the deformation resistance when brazing after processing is secured. In order to achieve this, it is understood that both the adjustment of the crystal grain structure (fibrous structure) and the suppression of the density of second phase particles with an equivalent circle diameter of 5 μm to 10 μm (1000 pieces / mm ² or less) are required.

  And in the comparative example 9, since the heating temperature of the heating process before hot rolling was too low, rolling became difficult and productivity became x. In Comparative Example 10, the reduction ratio of cold rolling (final cold rolling) was high, and the n value was too low, so the deformation resistance after processing was x.

  As described above, the present invention is an aluminum alloy material having a heat bonding function in a single layer, and is a material excellent in deformation resistance when brazed after processing according to the prior art. This deformation resistance is maintained even when the degree of processing before brazing is high. The present invention is useful as a constituent material of various aluminum material products such as heat exchangers and heat sinks. And, since it has a heat bonding function in a single layer, the product can be supplied at lower cost than the application of a brazing sheet or a brazing material.

Claims (7)

Si: 1.5% by mass to 5.0% by mass, Mn: 0.05% by mass to 2.0% by mass, Fe: 0.01% by mass to 2.0% by mass, balance Al and unavoidable It is an aluminum alloy material consisting of impurities and having a single layer heat bonding function,
The number density of the second phase particles having a fibrous structure and made of a Si-based compound or an AlMnFeSi-based compound and having an equivalent circle diameter of 5.0 μm to 10.0 μm is 1,000 / mm ² or less,
From the nominal strain of 0.9 times the nominal strain at the maximum load point to the nominal strain at the maximum load point, the work hardening index n value between two points is 0.03 or more,
Aluminum alloy material with a local elongation of 1% or more. Furthermore, the aluminum alloy material which has a heating joining function by the single | mono layer of Claim 1 containing the following 1 type, or 2 or more types of elements.
Zn: 0.05 to 6.0%,
Mg: 0.05 to 2.0%
Cu: 0.05 to 1.5%
Ni: 0.05 to 2.0%
Cr: 0.05 to 0.3%
Zr: 0.05 to 0.3%
Ti: 0.05 to 0.3%
V: 0.05 to 0.3% Furthermore, the aluminum alloy material which has a heating joining function by the single | mono layer of Claim 1 or 2 which contains following 1 type or 2 types of elements.
In: 0.005 to 0.3%
Sn: 0.005 to 0.3% Furthermore, the aluminum alloy material which has a heating joining function by the single | mono layer in any one of the Claims 1-3 which contain following 1 type, or 2 or more types of elements.
Be: 0.0001 to 0.1%
Sr: 0.0001 to 0.1%
Bi: 0.0001 to 0.1%
Na: 0.0001 to 0.1%
Ca: 0.0001 to 0.05% It is a manufacturing method of the aluminum alloy material in any one of Claims 1-4,
The casting process which manufactures a slab by DC casting,
A step of performing hot rolling after performing either the homogenization treatment step or the heating step of heating before hot rolling without performing the homogenization treatment after the casting step;
Cold rolling after the hot rolling process;
At least one annealing step performed during the cold rolling step;
The casting speed of the casting process is set to 20 to 100 mm / min.
The conditions of the heating step before the homogenization treatment step or the hot rolling are a heating temperature of 350 ° C. to 480 ° C., and a holding time of 0 to 30 hours.
The manufacturing method of the aluminum alloy material which carries out annealing at the temperature and time which do not produce recrystallization at the said annealing process. It is a manufacturing method of the aluminum alloy material which has a heating joining function by the single | mono layer in any one of Claims 1-4,
A casting process for producing a plate-like ingot by continuous casting;
A homogenization process performed after the casting process;
Cold rolling after the homogenization treatment step;
At least one annealing step performed during the cold rolling step;
The casting speed of the casting process is 500 to 3000 mm / min,
The conditions of the homogenization treatment step are a heating temperature of 350 ° C. to 480 ° C., and a holding time of 1 to 10 hours.
The manufacturing method of the aluminum alloy material which carries out annealing at the temperature and time which do not produce recrystallization at the said annealing process.   The manufacturing method of the aluminum alloy material of Claim 5 or 6 which cold-rolls after an annealing process and makes the working ratio in the said cold process 20% or less.