Assembly for brazing heat treatment

Abstract

To provide an assembly for brazing heat treatment.SOLUTION: First members 3, 4, 5 comprise a core material and a brazing material made of a melting member cladded on the core material, and a second member 2 comprises a substrate made of a member to be molten, wherein the melting member contains Si in an amount of 1.5 mass% or more and 14.0 mass% or less, one of V and Ti in an amount of 0.010 mass% or more and 1.5 mass% or less, with the balance consisting of Al and inevitable impurities, the member to be molten contains the other one of V and Ti in an amount of 0.010 mass% or more and 0.5 mass% or less, with the balance consisting of Al and inevitable impurities, an RD-TD parallel surface of the melting member has less than 5 intermetallic compounds containing one of V and Ti having a diameter of 10.00 μm or more in a circle equivalent diameter in an observation visual field of 10000 μm2, and an RD-TD parallel surface or an ED-TD parallel surface of the member to be molten has 10 or more intermetallic compounds containing the other one of V and Ti having a diameter of 0.01 μm or more and less than 5.00 μm in a circle equivalent diameter in an observation visual field of 10000 μm2.SELECTED DRAWING: Figure 1

Description

[Technical Field]

[0001] The present invention relates to an assembly for a brazing heat treatment. [Background technology]

[0002] Brazing is used to join the various components of automotive heat exchangers manufactured using aluminum alloys. Brazing is performed by using a brazing sheet made of an Al-Si alloy with a solidus temperature of 580°C or less, attached to a core material, and then melting only the brazing material through heat treatment at around 600°C. The molten brazing material flows between the components and cools, achieving a strong metallic bond. [Prior art documents] [Patent documents]

[0003] [Patent Document 1] JP 2007-182602 A, paragraph (0019) [Patent Document 2] JP 2010-107108 A, paragraph (0020) [Patent Document 3] JP 2011-140040 A, paragraph (0040) Summary of the Invention [Problem to be solved by the invention]

[0004] Conventional brazing is an excellent technology that can firmly join many joints at once, but it also presents several challenges. Brazing involves high-temperature heat treatment of a heat exchanger structure, but because the components vary in thickness, size, arrangement, and shape, there are differences in the rate at which they heat up. In other words, components that heat up easily may be exposed to a high-temperature environment for longer than components that heat up more slowly, or they may even heat up too much. When this happens, the molten brazing filler metal may continue to flow locally or concentrate in one area, eroding the components, and if the erosion becomes excessive, the components may become defective.

[0005] To prevent this corrosion, the brazing alloy of Patent Document 1 contains 5.0 to 13.0 mass% Si, 0.05 to 1.0 mass% Ti, 0.1 to 2.0 mass% Mn, and 0.01 to 0.5 mass% Zr, and may further contain 0.05 to 1.0 mass% Cr as needed, with the remainder being Al and unavoidable impurities, thereby reducing the fluidity of the molten brazing material. Materials that reduce the fluidity of such molten brazing material have been developed, but the structures to be brazed include a variety of components and arrangements, and the effect may not be sufficient.

[0006] Furthermore, Patent Documents 2 and 3 disclose that the temperatures of the header and tube are controlled during the brazing heat treatment process to prevent erosion of the tube by molten brazing brazing from the header. However, this is not easy to apply to various components with different thicknesses, sizes, arrangements, and shapes, and it is therefore desirable to improve productivity and the degree of freedom in controlling the brazing process.

[0007] SUMMARY OF THE INVENTION It is therefore an object of the present invention to provide an assembly for brazing heat treatment. [Means for solving the problem]

[0008] The inventors of the present application have succeeded in developing an assembly in connection with the manufacture of heat exchangers, which reduces erosion of the melted component by the melted brazing material produced by the melting component, even when exposed to high temperatures, by using an assembly in which an assembly made up of multiple components is heat treated to braze the multiple components, in which the melting component of one of the components to be assembled contains V and the melted component of the other component contains Ti, or in which the melting component of one component contains Ti and the melted component of the other component contains V, and further in which the melting component and the melted component each contain V, with the distribution of compounds containing V or Ti controlled.

[0009] The present invention provides an assembly for brazing heat treatment, which includes a first member and a second member assembled with the first member, wherein the first member includes a core material and a brazing filler metal made of a melting material clad on one or both sides of the core material directly or via an intermediate layer, and the second member includes at least a base material made of a member to be melted, the melting material containing 1.5% by mass or more and 14.0% by mass or less of Si, 0.010% by mass or more and 1.5% by mass or less of one of V and Ti, and the balance being Al and unavoidable impurities, and the member to be melted contains 0.010% by mass or more and 0.5% by mass or less of the other of V and Ti, and the balance being Al and unavoidable impurities, and the RD-TD parallel plane of the melting material has a thickness of 10,000 μm. 2 In the observation field of the present invention, there are less than five intermetallic compounds having a circle equivalent diameter of 10.00 μm or more and containing one of the two, and the RD-TD parallel plane or ED-TD parallel plane of the melted material is 10,000 μm 2 The present invention is characterized in that, in the observation field, there are 10 or more intermetallic compounds each having a circle-equivalent diameter of 0.01 μm or more and less than 5.00 μm and containing the other intermetallic compound.

[0010] Specifically, when the melting member contains one of V and Ti and the melted member contains the other of V and Ti, if the melting member contains V, the melted member contains Ti, and when the melting member contains Ti, the melted member contains V.

[0011] [Melting material] Si: 1.5% by mass or more and 14.0% by mass or less Silicon is added to form a fillet at the joint during brazing. If the silicon content is less than 1.5 mass%, the brazing filler will be insufficient and the joint will be insufficient. If the silicon content exceeds 14.0 mass%, the material will become hard and brittle, making it difficult to manufacture.

[0012] Ti: 0.010 mass% or more and 1.5 mass% or less When the melting material melts and corrodes the material to be melted, the Ti in the melting material forms a high-melting-point compound with the V contained in the material to be melted at the interface between the melting material and the material to be melted, reducing the corrosion of the material to be melted by the molten material (hereinafter, the "molten material" may be referred to as the melting furnace). If the Ti content is less than 0.010% by mass, the effect is insufficient, and if the Ti content exceeds 1.5% by mass, coarse intermetallic compounds are formed during casting, reducing rollability.

[0013] V: 0.010 mass% or more and 1.5 mass% or less When the melting material melts and corrodes the material to be melted, the V in the melting material forms a high-melting-point compound with the Ti contained in the material to be melted at the interface between the melting material and the material to be melted, reducing the corrosion of the material to be melted. If the V content is less than 0.010 mass%, the effect is insufficient, and if the V content exceeds 1.5 mass%, coarse intermetallic compounds are formed during casting, reducing rollability.

[0014] The RD-TD parallel plane of the fused material has a circle equivalent diameter of 10.00 μm or more, and a 10,000 μm diameter of an intermetallic compound containing either V or Ti. 2 The distribution of coarse intermetallic compounds is controlled by limiting the number of particles per unit area to less than 5. RD is the rolling direction, TD is the transverse direction perpendicular to the RD and the normal direction, and the RD-TD parallel plane of the molten material is a plane parallel to the rolling direction and the transverse direction, and is a plane formed by scraping the surface of the molten material (brazing filler metal) of the first member.

[0015] If the intermetallic compound containing either V or Ti in the melting material is coarse, the intermetallic compound is difficult to decompose when the melting material melts, the amount of V or Ti in the molten brazing material is reduced, and when the melting material takes in the melted material, sufficient reaction with the other of V and Ti contained in the melted material is not achieved, making it impossible to reduce erosion of the melted material by the brazing material.

[0016] [Melted material] Ti: 0.010 mass% or more and 0.5 mass% or less When the melting material melts and corrodes the material to be melted, the Ti in the material to be melted forms a high-melting-point compound with the V contained in the melting material at the interface between the melting material and the material to be melted, reducing the corrosion of the material to be melted. If the Ti content is less than 0.010 mass%, the effect is insufficient, and if the Ti content exceeds 0.5 mass%, coarse intermetallic compounds are formed during casting, reducing rollability.

[0017] V: 0.010 mass% or more and 0.5 mass% or less When the melting material melts and corrodes the material to be melted, the V in the material to be melted forms a high-melting-point compound with the Ti contained in the melting material at the interface between the melting material and the material to be melted, reducing the corrosion of the material to be melted. If the V content is less than 0.010 mass%, the effect is insufficient, and if the V content exceeds 0.5 mass%, coarse intermetallic compounds are formed during casting, reducing rollability.

[0018] The upper limits of the Ti and V contents of the melting member are set higher than the upper limits of the Ti and V contents of the melted member. When the Si content is high, the solidus temperature of aluminum drops significantly, which lowers the temperature at which compounds derived from Ti and V crystallize, and the V content or Ti content at which coarse intermetallic compounds form shifts to the higher side. Therefore, the upper limits of Ti and V in the melting material are higher than in the material to be melted.

[0019] The melted material is not limited to a material formed as a rolled material, but may be a material formed as an extruded material. The RD-TD parallel plane or ED-TD parallel plane of the melted material has a circle equivalent diameter of 0.01 μm or more and less than 5.00 μm, and the melted material has a circle equivalent diameter of 10,000 μm or more of an intermetallic compound containing V or Ti. 2The number of particles per unit area is set to 10 or more, and the distribution of fine intermetallic compounds is controlled. The RD-TD parallel plane of the melted material is a plane parallel to the rolling direction and the transverse direction, and is a plane formed by scraping the surface of the second material into the melted material (base material). In the ED-TD parallel plane of the melted material, ED is the extrusion direction, and TD is the transverse direction perpendicular to ED and the thickness direction (normal direction). The ED-TD parallel plane of the melted material is a plane parallel to the extrusion direction and the transverse direction, and is a plane formed by scraping the surface of the melted material (base material) of the second material.

[0020] In the melted material, fine intermetallic compounds containing V or Ti are removed to a size of 10,000 μm. 2 By distributing 10 or more per element, when the molten solder takes in the element to be melted, the element to be melted supplies the other of V and Ti to the molten solder containing one of V and Ti, and the one of Ti and V in the melting element and the other of V and Ti in the element to be melted form a compound, thereby reducing erosion of the element to be melted by the molten solder. 10,000 μm of intermetallic compounds in the melted material 2 If the number of perforations is less than 10, the erosion of the member to be melted by the brazing filler cannot be reduced.

[0021] In the assembly of the present invention, the melted member may further contain any one of the following additional elements 1 to 4, or any combination of a plurality of these elements.

[0022] The melted member further contains, as additive elements 1, 0.10 mass % to 2.0 mass % of Mn, 0.05 mass % to 1.5 mass % of Si, 0.05 mass % to 1.0 mass % of Fe, and 0.010 mass % to 2.0 mass % of Cu.

[0023] Mn: 0.10 mass% or more and 2.0 mass% or less When the melted material contains Mn, intermetallic compounds such as Al-Mn, Al-Mn-Si, and Al-Mn-Si-Fe compounds are precipitated, improving the strength of the material. If the Mn content is less than 0.10% by mass, the effect is insufficient, and if the Mn content exceeds 2.0% by mass, coarse intermetallic compounds are formed during casting, resulting in a decrease in rollability.

[0024] Si in the melted material: 0.05 mass% or more and 1.5 mass% or less Si in the material to be fused improves material strength through solid solution, and is added to improve material strength by precipitating as Al-Mn-Si or Al-Mn-Si-Fe intermetallic compounds. If the Si content of the material to be fused is less than 0.05 mass%, sufficient effect cannot be obtained, and if the Si content of the material to be fused exceeds 1.5 mass%, the solidus temperature drops and the material to be fused will not be able to maintain its shape during brazing.

[0025] Fe: 0.05 mass% or more and 1.0 mass% or less Fe is added to improve material strength by precipitating as intermetallic compounds such as Al-Mn-Fe and Al-Mn-Si-Fe. If the Fe content is less than 0.05% by mass, costs increase, while if the Fe content exceeds 1.0% by mass, coarse intermetallic compounds (crystallized particles) form during casting, reducing rollability.

[0026] Cu: 0.010 mass% or more and 2.0 mass% or less Cu is added to form a solid solution to improve material strength. If the Cu content is less than 0.010 mass%, the effect is insufficient, but if the Cu content exceeds 2.0 mass%, the material strength becomes too high, making it difficult to manufacture the material.

[0027] The melted member further contains, as an additional element 2, 0.01 mass % or more and 1.0 mass % or less of Mg.

[0028] Mg: 0.01 mass% or more and 1.0 mass% or less Mg is added to improve material strength by precipitating as a solid solution or intermetallic compounds such as Mg2Si. If the Mg content is less than 0.01% by mass, the effect is insufficient, while if the Mg content exceeds 1.0% by mass, the material strength becomes too high, making it difficult to manufacture the material.

[0029] The melted member further contains Zn as an additional element 3 in an amount of 0.01 mass % or more and 5.0 mass % or less.

[0030] Zn in the melted material: 0.01% by mass or more and 5.0% by mass or less Zn in the melted member is added to reduce the corrosion rate of the sacrificial protective material by dissolving and making the natural potential more base, thereby controlling the potential difference with the sacrificial protective material. If the Zn content of the melted member is less than 0.01% by mass, the effect is insufficient, and if the Zn content of the melted member exceeds 5.0% by mass, the potential becomes too base, reducing the self-corrosion resistance.

[0031] The melted member further contains, as an additional element 4, at least one element selected from the group consisting of 0.01 mass % to 0.35 mass % of Cr, 0.01 mass % to 0.35 mass % of Zr, and 0.01 mass % to 1.0 mass % of Sr.

[0032] Cr: 0.01 mass% or more and 0.35 mass% or less Cr is added to form intermetallic compounds to improve material strength. If the Cr content is less than 0.01% by mass, the effect is insufficient, while if the Cr content exceeds 0.35% by mass, coarse intermetallic compounds are formed during casting, reducing rollability.

[0033] Zr: 0.01 mass% or more and 0.35 mass% or less Zr is added to form intermetallic compounds to improve material strength. If the Zr content is less than 0.01% by mass, the effect is insufficient, while if the Zr content exceeds 0.35% by mass, coarse intermetallic compounds are formed during casting, reducing rollability.

[0034] Sr: 0.01 mass% or more and 1.0 mass% or less Sr is added to form intermetallic compounds to improve material strength. If the Sr content is less than 0.01% by mass, the effect is insufficient, while if the Sr content exceeds 1.0% by mass, coarse intermetallic compounds are formed during casting, reducing rollability.

[0035] In the assembly for brazing heat treatment of the present invention, the melting member preferably further contains 0.01 mass % or more and 5.0 mass % or less of Zn.

[0036] Zn: 0.01 mass% or more and 5.0 mass% or less Zn forms a potential gradient through solid solution and diffusion that causes the natural potential to change from noble to noble from the surface layer of the material in the depth direction, causing the corrosion to become planar, significantly improving the through-thickness life during material corrosion. If the Zn content is less than 0.01% by mass, sufficient effect cannot be obtained, and if the Zn content exceeds 5.0% by mass, the potential becomes excessively noble, increasing the rate of self-corrosion.

[0037] The method for manufacturing a brazed product of the present invention comprises a first member manufacturing step of manufacturing a first member having a brazing material made of a melting material clad on one or both sides thereof, a second member manufacturing step of manufacturing a second member made of a melting material, an assembly step of assembling the first member and the second member to assemble an assembly, and a heat treatment step of brazing the assembly, wherein the first member manufacturing step is performed at a pouring temperature of 640°C or higher but lower than 710°C and at a cooling rate of 0.10°C / s or higher. The method includes an ingot manufacturing process for manufacturing an ingot for a molten part, a homogenizing process for homogenizing the ingot for a molten part by maintaining the temperature of the ingot for a molten part at 400°C or higher but lower than 510°C, a facing process for facing the ingot for a molten part, a soaking process for soaking the faced ingot for a molten part, a hot rolling process for rolling the soaked ingot for a molten part with a hot rolling equivalent strain ε shown in the following (i) greater than 2.0, and assembling the brazing filler metal manufactured in the hot rolling process into a plate-shaped slab for a core material. and a cladding step of rolling and bonding these together to form the first member, wherein the second member manufacturing step includes an ingot manufacturing step of manufacturing an ingot for a second member, a homogenizing step of homogenizing the ingot for the second member by maintaining it at a temperature of 400°C or more and less than 600°C, a facing step of facing the ingot for the second member, a soaking step of soaking the faced ingot for the second member, and a hot rolling step of hot rolling the soaked ingot for the second member at a rolling time of 5°C / min or more. and a cold rolling process in which the thick plate formed in the hot rolling process is cold-rolled at a rolling reduction of 25% or more, wherein the ingot for the molten member contains 1.5% by mass to 14.0% by mass of Si, 0.010% by mass to 1.5% by mass of one of V and Ti, and the balance being Al and unavoidable impurities, and the ingot for the second member contains 0.010% by mass to 0.5% by mass of the other of V and Ti, and the balance being Al and unavoidable impurities. ε=(2 / √3)ln(t0 / t) (i) Here, t0 is the thickness of the ingot for the molten part before the hot rolling process in the first part manufacturing process is performed, and t is the thickness of the thick plate finished after the hot rolling process in the first part manufacturing process.

[0038] In the first member manufacturing process, the manufacturing conditions of casting, homogenization treatment, and rolling are controlled. This makes it possible to prevent large coarse intermetallic compounds from being distributed in the molten member. Specifically, the RD-TD parallel plane of the molten member is 10,000 μm. 2 In the observation field, the number of coarse intermetallic compounds containing either V or Ti and having a circle equivalent diameter of 10.00 μm or more is controlled to less than 5.

[0039] In the second member manufacturing process, the manufacturing conditions of the homogenization treatment and rolling are controlled. This allows for the fine intermetallic compounds to be densely distributed in the melted member. Specifically, the RD-TD parallel plane of the melted member is 10,000 μm. 2 In the observation field, 10 or more fine intermetallic compounds having a circle-equivalent diameter of 0.01 μm or more and less than 5.00 μm and containing the other of V and Ti are controlled.

[0040] The second member may be a core material made of a meltable member clad with a brazing filler metal or a sacrificial material on one or both sides thereof, either directly or via an intermediate layer. In this case, the second member manufacturing process includes an ingot manufacturing process for manufacturing an ingot for the meltable member (a plate-shaped slab), a homogenizing process for homogenizing the ingot for the meltable member by maintaining it at a temperature of 400°C or higher but lower than 600°C, a facing process for facing the ingot for the meltable member, a soaking process for assembling a rolled material for the brazing filler metal or a rolled material for the sacrificial material to the faced ingot for the meltable member and then soaking the resultant ingot, a hot rolling process for hot rolling the ingot for the meltable member and the rolled material for the brazing filler metal or the rolled material for the sacrificial material at a rolling time of 5°C / min or more and bonding them together to form a clad material, and a cold rolling process for cold rolling the clad material formed in the hot rolling process at a rolling reduction of 25% or more.

[0041] The ingot for the melted member may be formed by adding any one of the additional elements 1 to 4 or any combination of a plurality of additional elements. [Effects of the Invention]

[0042] According to the present invention, one of the V and Ti of the melting material can be sufficiently reacted with the other of the V and Ti of the material to be melted to form a compound with a high melting point, thereby reducing erosion of the material to be melted by the molten solder. [Brief explanation of the drawings]

[0043] [Figure 1] 1 is a diagram showing a heat exchanger according to an embodiment of the present invention; [Figure 2] FIG. 2 is a diagram for explaining a test method for erosion resistance in Example 1. DETAILED DESCRIPTION OF THE INVENTION

[0044] Hereinafter, an embodiment of the heat exchanger will be described with reference to the drawings. The heat exchanger 1 shown in Figure 1 is configured to include multiple tubes 2 through which a fluid acting as a heat transfer medium passes, fins 3 that come into contact with the outer surfaces of the tubes 2 to dissipate heat, and a set of headers 4 and 5 that distribute and supply the fluid to each tube 2 and reassemble the fluid that has passed through each tube. Between the two headers 4, 5 arranged parallel to each other in the vertical direction, the tubes 2 are arranged parallel to each other at intervals in the longitudinal direction (vertical direction) of the headers 4, 5, and both ends of each tube 2 are fixed to each header 4, 5 so that they communicate with the interior of the headers 4, 5, and fins 3 are arranged between each tube 2.

[0045] The tubes 2, fins 3, and headers 4 and 5 that constitute the heat exchanger 1 are each brazed. The headers 4 and 5 are first members having a brazing material made of a melting material to be described later, and the tube 2 is a second member having a base material made of a meltable material to be described later.

[0046] The manufacturing method for the heat exchanger 1 includes an assembly process in which the first and second members are assembled into an assembly, and a heat treatment process in which the assembly is subjected to a brazing heat treatment. In the assembly process, the first and second members are assembled into an assembly similar to that shown in FIG. 1. In the heat treatment process, the entire assembly is placed in a high-temperature furnace and subjected to a brazing heat treatment, followed by cooling. In this heat treatment process, the brazing material of the first member melts, brazing the contact portions of the first and second members, thereby forming the heat exchanger 1 as a brazed product. The brazing heat treatment conditions are heating to 600°C at an average heating rate of 100°C / min, holding at 600°C for 3 minutes, then cooling to 150°C at a cooling rate of 100°C / min, and then air-cooling to room temperature. During this heat treatment, the assembly is exposed to nitrogen gas in the heating furnace, with the nitrogen gas supplied at a rate of 150 liters / min. The above-described component configuration of the heat exchanger and the conditions of the brazing heat treatment are merely examples of the embodiment, and are not particularly limited to these.

[0047] In the assembly used to manufacture the heat exchanger of this embodiment, the melting element of the first member contains one of V and Ti, and the melted element of the second member contains the other of V and Ti. Specifically, when the melting element contains V, the melted element contains Ti, and when the melting element contains Ti, the melted element contains V. Hereinafter, a combination in which the melting element contains V and the melted element contains Ti may be referred to as a "melted V-melted Ti type," and a combination in which the melting element contains Ti and the melted element contains V may be referred to as a "melted Ti-melted V type."

[0048] The first component is made of a brazing sheet. Specifically, the brazing sheet includes a core material and a brazing filler metal made of a fusible material clad on one or both sides of the core material, either directly or via an intermediate layer. In a single-sided brazing clad brazing sheet in which the brazing filler metal is provided on one side, the side opposite the brazing filler metal may be formed of a sacrificial material. Specifically, in a two-layer structure, the first component is brazing filler metal / core material, and in a three-layer structure, it is brazing filler metal / core material / brazing filler metal or brazing filler metal / core material / sacrificial material. An intermediate layer may be interposed between the brazing filler metal and the core material, or between the core material and the sacrificial material, to form a structure of three or more layers. Note that in a double-sided brazing clad brazing sheet, one brazing filler metal is not limited to a fusible material, and may be formed of a conventional Al-Si aluminum alloy or the like.

[0049] The second member may be composed of a single layer of a substrate made of a material to be melted, or may comprise a substrate made of a material to be melted and a brazing material or sacrificial material clad on one or both sides of the substrate, either directly or via an intermediate layer. Specifically, a two-layer structure may be brazing material / core material or sacrificial material / core material, while a three-layer structure may be brazing material / core material / brazing material, brazing material / core material / sacrificial material, or sacrificial material / core material / sacrificial material. An intermediate layer may be interposed between the brazing material and core material, or between the core material and sacrificial material, to form a structure of four or more layers. The brazing material provided in the second member is not limited to the fusible material, and may be made of a conventional Al-Si based aluminum alloy.

[0050] Hereinafter, an example will be described in which the first member is made of a brazing sheet of a single-sided brazing clad type, and the second member is made of a single layer of substrate.

[0051] [Melting material] The composition of the molten material is 1.5 mass % to 14.0 mass % Si, 0.010 mass % to 1.5 mass % V or Ti, and the balance is Al and unavoidable impurities.

[0052] Si: 1.5% by mass or more and 14.0% by mass or less Silicon is added to form a molten braze when brazing the first and second components, forming a fillet at the joint. If the Si content is less than 1.5% by mass, there will be insufficient molten braze. If the Si content exceeds 14.0% by mass, the material will become hard and brittle, making it difficult to manufacture.

[0053] V: 0.010 mass% or more and 1.5 mass% or less When the molten brazing filler metal from the melting part of the first component erodes the melted part of the second component, the V in the molten brazing filler metal forms a high-melting point compound with Ti contained in the melted part at the interface between the melting part and the melted part, reducing the erosion of the melted part. If the V content is less than 0.010% by mass, the effect is insufficient, and if the V content exceeds 1.5% by mass, coarse intermetallic compounds are formed during casting, reducing rollability.

[0054] Ti: 0.010 mass% or more and 1.5 mass% or less When the molten brazing filler metal from the melting part of the first component erodes the melted part of the second component, the Ti in the molten brazing filler metal forms a high-melting point compound with the V contained in the melted part at the interface between the melting part and the melted part, reducing the erosion of the melted part. If the Ti content is less than 0.010% by mass, the effect is insufficient, and if the Ti content exceeds 1.5% by mass, coarse intermetallic compounds are formed during casting, reducing rollability.

[0055] The RD-TD parallel plane of the fusion material has a circle equivalent diameter of 10.00 μm or more, and a 10,000 μm diameter of an intermetallic compound containing V or Ti. 2 The distribution of coarse intermetallic compounds is controlled by limiting the number of particles per unit area to less than 5. The RD-TD parallel surface of the fusion member is a surface parallel to the RD (rolling direction) and TD (transverse direction), and is formed by scraping the surface of the fusion member (brazing filler metal) of the first member. If the intermetallic compounds containing V or Ti in the melting material are coarse, the intermetallic compounds will be difficult to decompose when the melting material melts. If the amount of V or Ti in the molten brazing filler metal is reduced, the V in the molten brazing filler metal will not react sufficiently with the Ti in the melted material, or the Ti in the molten brazing filler metal will not react sufficiently with the V in the melted material, and the erosion of the melted material by the molten brazing filler metal will not be reduced.

[0056] [Melted material] The composition of the material to be melted contains 0.010 mass % or more and 0.5 mass % or less of V or Ti, with the remainder being Al and unavoidable impurities.

[0057] V: 0.010 mass% or more and 0.5 mass% or less When the molten brazing filler metal from the melting part of the first component erodes the melted part of the second component, the V in the melted part forms a high-melting point compound with Ti contained in the molten brazing filler metal at the interface between the melting part and the melted part, reducing the erosion of the melted part. If the V content is less than 0.010% by mass, the effect is insufficient, and if the V content exceeds 0.5% by mass, coarse intermetallic compounds are formed during casting, reducing rollability.

[0058] Ti: 0.010 mass% or more and 0.5 mass% or less When the molten filler metal from the first component erodes the melted component of the second component, the Ti in the melted component forms a high-melting-point compound with the V contained in the molten filler metal at the interface between the melted component and the melted component, reducing the erosion of the melted component. If the Ti content is less than 0.010% by mass, the effect is insufficient, and if the Ti content exceeds 0.5% by mass, coarse intermetallic compounds are formed during casting, reducing rollability.

[0059] The upper limits of the V and Ti contents of the melting material are set higher than the upper limits of the V and Ti contents of the material to be melted. This is because a high Si content significantly lowers the solidus temperature of aluminum, and this lowering of the temperature at which V-derived compounds or Ti-derived compounds crystallize lowers, shifting the V content or Ti content at which coarse intermetallic compounds form to a higher value.

[0060] The RD-TD parallel plane of the melted material has a circle equivalent diameter of 0.01 μm or more and less than 5.00 μm, and a 10,000 μm diameter of an intermetallic compound containing V or Ti. 2 The distribution of fine intermetallic compounds is controlled by setting the number of particles per unit area to 10 or more. The RD-TD parallel surface of the material to be melted is a surface parallel to the RD (rolling direction) and TD (transverse direction), and is a surface formed by scraping the surface of the second material down to the inside of the material to be melted (base material).

[0061] In the melted material, fine intermetallic compounds containing V or Ti are removed to a size of 10,000 μm. 2 By distributing 10 or more per 10000 μm of intermetallic compounds in the material to be melted, when the molten brazing filler metal takes in the material to be melted, the material to be melted supplies the other of V and Ti to the molten brazing filler metal containing one of V and Ti. This allows the V in the molten brazing filler metal to react with the Ti in the material to be melted to form a compound, or the Ti in the molten brazing filler metal to react with the V in the material to be melted to form a compound, thereby reducing the erosion of the material to be melted by the molten brazing filler. 2 If the number of holes per hole is less than 10, it is not possible to reduce the erosion of the member to be melted by the molten brazing filler.

[0062] (Manufacturing method of first member) The method for manufacturing the first member includes a brazing material manufacturing step and a clad material manufacturing step.

[0063] A. Brazing material manufacturing process The brazing material manufacturing process includes an ingot manufacturing process for manufacturing ingots for molten parts, a homogenizing process for homogenizing the ingots, a facing process for facing the ingots, a soaking process for soaking the faced ingots, and a hot rolling process for rolling the soaked ingots.

[0064] A-1. Ingot manufacturing process The ingot manufacturing process involves producing ingots (plate-shaped slabs) by casting. The ingot for brazing filler metal is made of an aluminum alloy containing 1.5 mass % to 14.0 mass % of Si, 0.010 mass % to 1.5 mass % of V or Ti, and the balance being Al and unavoidable impurities. The casting temperature is 640°C or higher and lower than 710°C, preferably 660°C or higher and lower than 690°C. If the casting temperature is lower than 640°C, the time spent in the crystallization temperature range during casting is prolonged, resulting in the formation of coarse intermetallic compounds that cannot be sufficiently crushed during the rolling process. If the casting temperature is higher than 710°C, molten metal leakage will occur, making production impossible.

[0065] The cooling rate is 0.10°C / sec or more, preferably 1°C / sec or more. If the cooling rate during casting is less than 0.10°C / sec, the time spent in the crystallization temperature range during casting will be long, and coarse intermetallic compounds will be generated that cannot be sufficiently crushed in the rolling process.

[0066] To improve the corrosion resistance of the molten material (brazing filler metal), the ingot may be produced by adding Zn, with the amount of Zn added being 0.01% by mass or more and 5.0% by mass or less.

[0067] A-2. Homogenization process In the homogenization step, the ingot is heated to a temperature of 400° C. or higher and lower than 510° C., and preferably maintained at a temperature of 430° C. or higher and lower than 490° C. The holding time is 1 hour or longer and 3 hours or shorter. The homogenization process rounds the corners of the eutectic Si in the ingot, improving the strength of the molten material and extending its lifespan. Homogenization at temperatures below 400°C does not provide the desired strength to the molten material. Homogenization at temperatures above 510°C causes the shape of the coarse intermetallic compounds containing V or Ti to become spherical, making them less likely to be crushed during the subsequent rolling process.

[0068] A-3. Facing process In the facing process, the top and bottom surfaces of the ingot are faced to remove segregated areas and oxide films.

[0069] A-4.Soaking process The temperature and time of the soaking step are not limited, but for example, the ingot is held at a temperature of 430°C to 530°C for 1 hour to 12 hours before processing.

[0070] A-5. Hot rolling process In the hot rolling step, the soaked ingot is rolled to form a first rolled material, which is used as a brazing filler metal.

[0071] [Equivalent strain in hot rolling] In the hot rolling process, the condition is that the equivalent strain ε in the hot rolling, as shown in the following formula (1), exceeds 2.0 (ε>2.0). ε=(2 / √3)ln(t0 / t) Equation (1) Here, t0 is the thickness of the slab (face-ground ingot) before the hot rolling process, and t is the thickness of the plate finished after the hot rolling process. By controlling the hot rolling so as to satisfy the above condition (ε>2.0), it is possible to crush the coarse intermetallic compounds generated during casting.

[0072] There are no limitations on the manufacturing method or conditions for the core plate slab (ingot) as long as it is suitable for cladding the first rolled material.

[0073] B. Clad material manufacturing process The clad material manufacturing process includes an assembly process in which the first rolled material is assembled to a core plate slab; a soaking process in which the first rolled material and the core plate slab are soaked in a state in which they are stacked after the assembly process; a hot rolling process in which the first rolled material and the core plate slab are rolled and bonded together to form a clad material; and a cold rolling process in which the clad material formed in the hot rolling process is thinned. After the cladding process, a brazing sheet is completed in which the brazing material (melting material) is clad on the core material.

[0074] If necessary, intermediate annealing may be performed on the clad material between the hot rolling process and the cold rolling process, or during the cold rolling process, and final annealing may be performed on the clad material after the cold rolling process. The intermediate annealing and final annealing are performed, for example, by holding the temperature at 200°C to 450°C for 1 hour to 12 hours. If only intermediate annealing is performed, the brazing sheet will be tempered H1n, and if final annealing is performed, it will be tempered H2n or O depending on the annealing conditions.

[0075] C. Processing process In the processing step, the clad material is processed into a desired shape. Through this processing step, the first member (headers 4, 5) is completed.

[0076] (Manufacturing method of second member) The method for manufacturing the second member includes a second rolled material manufacturing step of manufacturing a second rolled material for the base material, and a processing step of processing the second rolled material into a desired shape.

[0077] D. Production of second rolling material for base material The second rolled material manufacturing process includes an ingot manufacturing process for manufacturing an ingot for the melted member, a homogenizing process for homogenizing the ingot, a facing process for facing the ingot, a soaking process for soaking the faced ingot, a hot rolling process for rolling the soaked ingot, and a cold rolling process for thinning the thick plate formed in the hot rolling process.

[0078] D-1. Ingot manufacturing process The ingot manufacturing process involves producing ingots (plate-shaped slabs) by casting. The ingot for the substrate is made of an aluminum alloy containing 0.010% by mass or more and 0.5% by mass or less of V or Ti, with the remainder being Al and unavoidable impurities. When the melted material contains V, the ingot for the substrate contains Ti, and when the melted material contains Ti, the ingot for the substrate contains V. The casting method is not particularly limited, and a conventional method can be used.

[0079] In order to improve the strength of the member to be melted (second member), the ingot may be formed by adding any one of the additional elements 1 to 4 or any combination of a plurality of additional elements.

[0080] The additive elements 1 are Mn, Si, Fe, and Cu. The additive amount of Mn is 0.10% by mass or more and 2.0% by mass or less, the additive amount of Si is 0.05% by mass or more and 1.5% by mass or less, the additive amount of Fe is 0.05% by mass or more and 1.0% by mass or less, and the additive amount of Cu is 0.010% by mass or more and 2.0% by mass or less.

[0081] The additional element 2 is Mg. The amount of Mg added is 0.01% by mass or more and 1.0% by mass or less.

[0082] The additional element 3 is Zn. The amount of Zn added is 0.01 mass % or more and 5.0 mass % or less.

[0083] The additional element 4 is any one or a combination of Cr, Zr, and Sr. The amount of Cr added is 0.01% by mass or more and 0.35% by mass or less, the amount of Zr added is 0.01% by mass or more and 0.35% by mass or less, and the amount of Sr added is 0.01% by mass or more and 1.0% by mass or less.

[0084] D-2. Homogenization process In the homogenization process, the ingot is heated to a temperature of 400°C or higher but lower than 600°C, and then maintained at a temperature of preferably 430°C or higher but lower than 580°C. The holding time is 1 hour or higher but 12 hours or lower, and preferably 3 hours or higher but 10 hours or lower. The homogenization treatment promotes the precipitation and growth of intermetallic compounds containing V or Ti. If the homogenization treatment temperature is lower than 400°C, sufficient precipitation and growth of intermetallic compounds cannot be obtained, while if the homogenization treatment temperature is higher than 600°C, the intermetallic compounds will grow coarsely.

[0085] D-3. Facing process In the facing process, the top and bottom surfaces of the ingot are faced to remove segregated areas and oxide films.

[0086] D-4.Soaking process In the soaking step, the faced ingot is soaked, but the temperature and time are not limited.

[0087] D-5. Hot rolling process In the hot rolling process, the faced ingot is rolled. In the hot rolling process, the rolling time between 400°C and 500°C is 5 minutes or more, preferably 10 minutes or more. By rolling for 5 minutes or more in the high temperature range between 400°C and 500°C, where dynamic strain is introduced, the precipitation of fine intermetallic compounds containing V or Ti and having a circle equivalent diameter of 0.01 μm or more and less than 5.00 μm is promoted in the melted material. If the rolling time between 400°C and 500°C is less than 5 minutes, the fine intermetallic compounds cannot be sufficiently distributed.

[0088] D-6. Cold rolling process In the cold rolling process, the reduction rate per pass is set to 25% or more for plate thicknesses of 0.5 mm or more, which crushes coarse intermetallic compounds containing V or Ti in the melted material and allows fine intermetallic compounds containing V or Ti to be densely distributed. After undergoing the cold rolling process, the second rolled material is formed into a base material (a member to be melted).

[0089] Furthermore, when the second member is constructed of a laminated material, the manufacturing method of the second member (second member manufacturing process) includes an ingot manufacturing process for manufacturing an ingot for the member to be melted (a plate-shaped slab), a homogenizing process for homogenizing the ingot for the member to be melted by maintaining it at a temperature of 400°C or higher but lower than 600°C, a facing process for facing the ingot for the member to be melted, a soaking process for assembling a brazing material or a sacrificial material to the faced ingot for the member to be melted and then soaking the resultant ingot, a hot rolling process for hot rolling the ingot for the member to be melted and the brazing material or the sacrificial material after the soaking process at a rolling time of 5°C / min or higher and bonding them together to form a clad material, and a cold rolling process for cold rolling the clad material formed in the hot rolling process at a rolling reduction of 25% or higher. The number of layers is not limited to two or three.

[0090] Intermediate annealing may be performed on the clad material between the hot rolling process and the cold rolling process, or during the cold rolling process, or final annealing may be performed on the clad material that has undergone the cold rolling process. Even when the second component is made of a single-layer second rolled material, final annealing may be performed on the second rolled material produced through the cold rolling process. Intermediate annealing and final annealing are performed, for example, by maintaining a temperature of 200°C to 450°C for 1 hour to 12 hours. If only intermediate annealing is performed on the clad material, it will be tempered H1n, and if final annealing is performed, it will be tempered H2n or tempered O depending on the annealing conditions.

[0091] E. Processing process In the processing step, the second rolled material is processed into a desired shape. After the processing step, a second member (tube 2) is completed.

[0092] The molten material of the first member manufactured as described above has a thickness of 10,000 μm on the RD-TD parallel surface. 2 The number of coarse intermetallic compounds containing V or Ti is controlled to less than 5 per unit area, which makes it easy to decompose the intermetallic compounds containing V or Ti. Furthermore, the melted material of the second member is 2 Since the number of fine intermetallic compounds containing V or Ti per unit area is tightly controlled to 10 or more, when the assembly is heat treated to braze the first and second components, even if, for example, the first components (headers 4, 5) are exposed to a high-temperature environment or the first components (headers 4, 5) become overheated, causing the molten brazing filler metal to flow locally and continuously from the first components (headers 4, 5) to the second components (tube 2), forming a brazing filler metal pool in the second component (tube 2), and causing the second component (tube 2) to be eroded by the molten brazing filler metal, the V contained in the molten brazing fills the Ti contained in the component to be eroded sufficiently to form a high-melting point compound at the interface between the melting component and the melting component, or the Ti contained in the molten brazing fills the V contained in the component to be eroded sufficiently to form a high-melting point compound at the interface between the melting component and the melting component, thereby reducing the erosion of the component to be eroded by the molten brazing filler. Therefore, the heat exchanger can be manufactured with reduced erosion by the molten brazing filler.

[0093] Previously, materials have been developed to prevent erosion of core materials by molten brazing filler metal, but these have not been sufficient. Brazing heat treatment requires enormous amounts of energy and precise control of factors such as temperature rise time, holding time, heat exchanger placement, and heat application method. The assembly of the present invention eliminates the need for precise control of heat treatment equipment, shortening the brazing process time and improving the flexibility of brazing process control. Furthermore, the assembly of the present invention uses a melting element and a melted element, reducing erosion of the melted element by molten brazing filler metal. This allows for the manufacture of heat exchangers with excellent strength and corrosion resistance, allowing for long-term use. This also contributes to energy savings in the brazing heat treatment process, which has become increasingly important in recent years as a means of reducing CO2 emissions.

[0094] The tube 2 as the second member made of the melted material in the above embodiment can also be manufactured as an extruded material. The manufacturing method of the extruded material includes an ingot manufacturing process similar to that of D-1, a homogenization process of homogenizing the ingot similar to that of D-2, and an extrusion process of extruding the ingot.

[0095] (Extrusion process) The extrusion process is a hot extrusion process. During extrusion, processing heat is generated by friction between the aluminum alloy and the die, causing the material temperature to rise. The maximum temperature reached during extrusion is, for example, less than 620°C, preferably less than 580°C. At temperatures above 620°C, the compounds become coarse and redissolve, resulting in a sparse distribution. The extrusion speed is 0.5 m / s or more. By setting the extrusion speed to 0.5 m / s or more, processing stress can be applied to the material, crushing the coarse intermetallic compounds.

[0096] The extrusion process completes the extruded material made of the melted material. The manufacturing method for the extruded material may include solution treatment, aging treatment, and brazing heat treatment as required.

[0097] The extruded material is made of an aluminum alloy containing 0.010% by mass or more and 0.5% by mass or less of V or Ti, with the remainder being Al and unavoidable impurities. When the melting component contains V, the extruded material contains Ti, and when the melting component contains Ti, the extruded material contains V. In order to improve the strength of the melted component (second component), the ingot for the extruded material may be cast by adding any one of the additive elements 1 to 4 or any combination of multiple elements. The tube 2 may have a laminated structure, including a substrate made of the extruded material and a Zn spray coating covering the surface of the substrate.

[0098] Whether the second member (tube 2) is a single-layer or multi-layer structure, the ED-TD parallel plane of the member to be melted is 10,000 μm 2 The observation field is characterized in that there are 10 or more intermetallic compounds having a circle equivalent diameter of 0.01 μm or more and less than 5.00 μm and containing V or Ti.

[0099] When a first component (header 4, 5) is assembled to a second component (tube 2) having a meltable component, which is an extruded material, and the first component and second component are brazed together, molten solder flows continuously and locally from the first component (header 4, 5) to the second component (tube 2), forming a solder pool in the second component (tube 2). Even if the molten solder erodes the meltable component of the second component (tube 2), the V contained in the molten solder and the Ti contained in the meltable component react sufficiently to form a high-melting point compound at the interface between the melting component and the meltable component, or the Ti contained in the molten solder and the V contained in the meltable component react sufficiently to form a high-melting point compound at the interface between the melting component and the meltable component, thereby reducing the erosion of the meltable component by the molten solder.

[0100] The present invention can be practiced without being limited to the above-described and illustrated examples.

[0101] In the above embodiment, the headers 4 and 5 are made of the melting member (first member) and the tube 2 is made of the melting member (second member) as the melting member (first member) and the melted member (second member) to which a large amount of brazing material can be supplied from the melting member (first member) during brazing heat treatment. However, the relationship between the melting member (first member) and the melted member (second member) is not limited to the header-tube relationship. For example, in the case of a tube-fin relationship such as that of a radiator or condenser, the tube corresponds to the melting member (first member) and the fin corresponds to the melted member (second member). In this case, even if the first member becomes overheated, the melting member (brazing material) of the first member melts and flows to the second member, forming a brazing material puddle on the second member, the V and Ti in the melting member (brazing material) sufficiently react with each other to form a high-melting-point compound, thereby reducing erosion of the melted member by the melting member (brazing material).

[0102] In a stacked heat exchanger such as an oil cooler, the plates correspond to the first and second members. [Example]

[0103] A first plate material clad with solder on one side and a second plate material consisting of a single layer were produced using different materials and manufacturing conditions.A first member cut out from the first plate material was assembled to a second member cut out from the second plate material, and a heat treatment equivalent to soldering was performed.The erosion caused by the solder material of the first member on the second member was evaluated.

[0104] (material) The combination of the first plate material and the second plate material is [melting V-melted Ti type] or [melting Ti-melted V type], and the contents of Si, V, Ti, and Zn in the material (ingot) of the melting member (brazing filler metal) are shown in Table 1, and the contents of V and Ti in the material (ingot) of the melting member that forms the second plate material are shown in Table 2. The remainder not shown in Tables 1 and 2 is aluminum and unavoidable impurities.

[0105] A. Materials for melting components (brazing materials) The melting materials 1 to 3, 7, and 8 are materials for the [melting V-melting Ti type], and the melting materials are aluminum alloys whose ingots contain 1.5 to 14.0 mass% Si, 0.010 to 1.5 mass% V, and the balance being Al and unavoidable impurities. The melting material 11 is obtained by further adding 0.01 to 5.0 mass% Zn to this composition. The melting materials 4 to 6, 9, and 10 are materials for the [molten Ti-molten V-shaped], and the melting materials are aluminum alloys whose ingots contain 1.5 to 14.0 mass% Si, 0.010 to 1.5 mass% Ti, and the balance being Al and unavoidable impurities. The melting material 12 is obtained by further adding 0.01 to 5.0 mass% Zn to this composition. Molten materials 14 to 17 are materials for [molten V-molten Ti type], but the Si content of the ingot is outside the range of 1.5 mass% or more and 14.0 mass% or the V content is outside the range of 0.010 mass% or more and 1.5 mass% or less. The molten materials 18 and 19 are materials for [molten Ti-molten V-shape], but the Ti content of the ingot is outside the range of 0.010 mass % or more and 1.5 mass % or less.

[0106] B. Material of the melted part Materials to be melted 1 to 3 are materials for [V melting - Ti melting type], and the ingot is made of an aluminum alloy containing 0.010 mass % to 0.5 mass % of Ti, the balance being Al and unavoidable impurities. Materials 4 to 6 to be melted are materials for [molten Ti-molten V type], and the ingot is made of an aluminum alloy containing 0.010 mass % to 0.5 mass % of V, the balance being Al and unavoidable impurities. Materials to be melted 17 and 18 are materials for the [V melting - Ti melting type], but the Ti content of the ingot is outside the range of 0.010 mass % or more and 0.5 mass % or less. The materials to be melted 19 and 20 are materials for [molten Ti-molten V-shape], but the V content of the ingot is outside the range of 0.010 mass % or more and 0.5 mass % or less.

[0107] [Table 1]

[0108] [Table 2]

[0109] (Manufacturing method) A. Manufacturing method of first plate material The first plate material is manufactured through a brazing material manufacturing process and a clad material manufacturing process. The brazing material manufacturing process includes an ingot manufacturing process for manufacturing an ingot, a homogenizing process for homogenizing the ingot, a facing process for facing the ingot, a soaking process for soaking the faced ingot, and a hot rolling process for rolling the soaked ingot.

[0110] In the ingot manufacturing process, an ingot (slab) having the composition shown in Table 1 was manufactured. The pouring temperature was 640°C or higher and lower than 710°C, and the cooling rate was 0.10°C / second or higher. In the homogenization process, the ingot is heated to a temperature of 400°C or higher but lower than 510°C and maintained at this temperature for a period of 1 hour or longer but 3 hours or shorter. Before the soaking process, the upper and lower surfaces of the ingot are chamfered in a chamfering process. In the soaking treatment step, the ingot is held at a temperature of 430°C or higher and 530°C or lower for 1 hour or higher and 12 hours or shorter before processing the ingot. After the soaking process, the ingot is hot-rolled to form a first rolled material (brazing filler metal). Note that the equivalent strain ε in the hot rolling, as shown in the above formula (1), must exceed 2.0 (ε>2.0). The core slabs are made of JIS 3000 series aluminum alloy. The clad material manufacturing process involves assembling a first rolled material (brazing material) to a core plate slab, rolling them together, and forming a first plate (brazing sheet). The first plate is 1 mm thick and has a single-sided brazing material with a cladding ratio of 10%, and is then subjected to final annealing at 60°C for 3 hours to produce a clad material with a temper of O. The first plate is then cut into a size of 60 mm long and 60 mm wide to form the first component. In this way, manufacturing methods A to C are manufacturing methods in which the manufacturing conditions for casting, homogenization treatment, and rolling are controlled to produce a first plate material. Note that manufacturing methods D to G do not control the manufacturing conditions for any of casting, homogenization treatment, and rolling. The manufacturing conditions for each manufacturing method are shown in Table 3.

[0111] [Table 3]

[0112] B. Manufacturing method of the second plate material The second plate material is produced through an ingot production process, a homogenization process for homogenizing the ingot, a facing process for facing the ingot, a soaking process for soaking the faced ingot, a hot rolling process for rolling the soaked ingot, and a cold rolling process for thinning the thick plate formed in the hot rolling process. In the ingot manufacturing process, ingots (plate-shaped slabs) having the compositions shown in Table 2 were manufactured. In the homogenization process, the ingot is heated to a temperature between 400°C and 600°C and maintained at this temperature for 8 hours. In the hot rolling process, the rolling time between 400°C and 500°C was set to 5 minutes or more. The plate was then cold-rolled to a thinner thickness, with a reduction rate of 25% or more per pass. The second plate material had a thickness of 1 mm and was subjected to final annealing at 360°C for 3 hours to achieve a temper O. A piece measuring 60 mm in length and 40 mm in width was cut out from this second plate material to serve as a second member. In this way, manufacturing methods a to c are manufacturing methods for producing second plate materials by controlling the manufacturing conditions of the homogenization treatment and rolling. In manufacturing methods d to f, the above manufacturing conditions of either the homogenization treatment or the rolling are not controlled. The manufacturing conditions of each manufacturing method are shown in Table 4.

[0113] [Table 4]

[0114] A first plate material was produced using a material (any of melting materials 1 to 19) and manufacturing conditions (any of manufacturing methods A to G), and a second plate material was produced using a material (any of melted materials 1 to 6, 17 to 20) and manufacturing conditions (any of manufacturing methods a to f).A first member cut out from the first plate material was assembled to a second member cut out from the second plate material to form assemblies called samples 1 to 3, 11, 12, 17 to 19, 24, 25, 27 to 68.Samples 1 to 3, 11, 12, 17 to 19, 24, 25, 27 to 68 were subjected to heat treatment equivalent to brazing, and the erosion resistance of samples 1 to 3, 11, 12, 17 to 19, 24, 25, 27 to 68 was evaluated. Before heat treatment was performed on Samples 1 to 3, 11, 12, 17 to 19, 24, 25, and 27 to 68, the compounds of the first and second members constituting Samples 1 to 3, 11, 12, 17 to 19, 24, 25, and 27 to 68 were measured.

[0115] [Number of compounds (distribution)] B. Coarse intermetallic compounds The surface layer of the first plate material of samples 1 to 3, 11, 12, 17 to 19, 24, 25, 27 to 68 was polished with abrasive grains of about 0.1 μm, and a fully automatic particle analysis of the surface layer was performed from the surface direction using an EPMA (electron probe microanalyzer). At the same time, a thin film was prepared by mechanically polishing and electrolytically polishing the sample pieces cut out from the molten material (brazing material) that constitutes the surface layer, and a 10,000 μm RD-TD parallel plane was observed using a TEM (transmission electron microscope). 2 The observation field was set to 100 μm square and the coarse compounds were measured. In the case of a V-melting type fusion material (brazing filler metal), the coarse compounds were those having a circle-equivalent diameter exceeding 10.00 μm and containing V. In the case of a Ti-melting type fusion material (brazing filler metal), the coarse compounds were those having a circle-equivalent diameter exceeding 10.00 μm and containing Ti.

[0116] B. Fine intermetallic compounds The surface layer of the second plate material of samples 1 to 3, 11, 12, 17 to 19, 24, 25, 27 to 68 was polished with abrasive grains of about 0.1 μm, and a fully automatic particle analysis of the surface layer was performed from the surface direction using an EPMA (electron probe microanalyzer). At the same time, a thin film was prepared by mechanically polishing and electrolytically polishing the cut-out sample pieces from the molten material (brazing material) that constitutes the surface layer, and a 10,000 μm RD-TD parallel plane was observed using a TEM (transmission electron microscope). 2 The fine compounds were measured using an observation field of view of 100 μm square. In the case of a V-fusion type melted material, the fine compounds were those having a circle-equivalent diameter of 0.01 μm to 5.00 μm and containing Ti. In the case of a Ti-fusion type melted material, the fine compounds were those having a circle-equivalent diameter of 0.01 μm to 5.00 μm and containing V. Table 5 shows the number of coarse compounds in the melting member (brazing filler metal) and the number of fine compounds in the melted member (second plate material).

[0117] [Erosion resistance] As shown in Figure 2, the second member 200 of the assembly has a groove 210 with a length of 50 mm and a cross section of 0.3 mm depth and 0.3 mm width formed by NC milling before final annealing. The assembly is also assembled with the first member 100 as the upper plate and the second member 200 as the lower plate, with one corner of the upper plate abutting the edge of the groove 210 and rising vertically from the lower plate. An aluminum fiber sintered body 300 measuring 30 mm in length and 20 mm in width was placed on the lower plate on the opposite side of the location where the upper plate was assembled, with the distance between the upper plate contact point P1 and the aluminum fiber sintered body 300 being 30 mm. The coating amount was 15 g / m 2 As a result, the flux was applied only to the aluminum fiber sintered body 300 and the groove 210 portion. In this assembled state in which the first member 100 (upper plate) stood up from the second member 200 (lower plate), the assembly was subjected to a heat treatment equivalent to brazing. The conditions for the heat treatment equivalent to brazing were heating to 600°C at an average heating rate of 100°C / min, holding at 600°C for 3 minutes, then cooling to 150°C at a cooling rate of 100°C / min, and then air-cooling to room temperature. During this heat treatment, the assembly was exposed to nitrogen gas in a heating furnace, and the nitrogen gas was supplied at a rate of 150 liters / min.

[0118] This heat treatment causes the molten material (brazing material) of the first member 100 to become molten brazing material, which flows from the first member 100 through the groove 210 of the second member 200 and is absorbed into the aluminum fiber sintered body 300. After the heat treatment, a cross section of a portion P2 of the groove 210 located 15 mm from the contact point P1 with the end of the groove 210 of the first member 100 (upper plate) was observed, and the area S1 mm of the hollow portion of the groove 210 was 2 This value S1 and the area of ​​the hollow part of the cross section of the initial groove 210, S0 mm 2 (=0.09mm 2 ) is the erosion area ΔS (= S1 - S0) mm 2 It was decided.

[0119] Erosion resistance is evaluated when the erosion area ΔS is 0.25 mm 2 Less than 0.25mm is good 2 More than 0.30mm 2 The erosion area ΔS is 0.30 mm or less, and the results are considered to be slightly good and pass. 2 The above were evaluated as poor (failed) and the erosion resistance was evaluated. The number of compounds measured and the evaluation of erosion resistance for Samples 1 to 3, 11, 12, 17 to 19, 24, 25, and 27 to 68 are shown in Table 5. In Table 5, A indicates good, B indicates fairly good, and C indicates poor.

[0120] [Table 5]

[0121] Samples 1 to 3, 27 to 30, 47, 48, 53 and 54 are of the V-melt type. The molten material (the brazing filler metal for the first plate material) is made from any one of molten materials 1, 2, 3, 7, and 8, which contains 1.5 mass% or more and 14.0 mass% or less of Si, 0.010 mass% or more and 1.5 mass% or less of V, with the remainder being Al and unavoidable impurities, by any one of manufacturing methods A to C, which control the manufacturing conditions of casting, homogenization treatment, and rolling. As a result, the RD-TD parallel plane of the molten material is 10,000 μm 2 In the observation field, the distribution of coarse intermetallic compounds containing V, each having an equivalent circle diameter of 10.00 μm or more, is controlled to less than 5 particles. The melted member (second plate material) is made from any of melted materials 1 to 3, which contain 0.010 mass% or more and 0.5 mass% or less of Ti, with the remainder being Al and unavoidable impurities, by any of manufacturing methods a to c, in which the manufacturing conditions of homogenization treatment and rolling are controlled. As a result, the RD-TD parallel plane of the melted member (second plate material) is 10,000 μm 2 In the observation field, 10 or more fine intermetallic compounds containing Ti and having a circle equivalent diameter of 0.01 μm or more and less than 5.00 μm are densely distributed. In the erosion resistance test, it was confirmed that the erosion of the melted material (second plate material) by the molten solder was reduced by allowing the V in the molten solder melted in the melting material (first plate material) to react sufficiently with the Ti in the melted material (second plate material) to form a high-melting point compound.

[0122] Sample 31 differs from Samples 1 to 3 in that the molten member (the brazing filler metal of the first plate material) uses molten material 11 further containing Zn in the range of 0.01 mass % to 5.0 mass %. The melting member (the brazing filler metal for the first plate material) is produced by manufacturing method A, which controls the manufacturing conditions for casting, homogenization treatment, and rolling. The melting member (the second plate material) is also produced by manufacturing method a, which controls the manufacturing conditions for homogenization treatment and rolling. In a test of the erosion resistance of Sample 31, it was confirmed that the erosion of the member to be fused (second plate material) by the molten brazing filler metal was reduced.

[0123] Samples 17 to 19, 37 to 40, 58, 59, 64 and 65 are Ti-fused types. The molten material (the brazing filler metal for the first plate material) is made from any one of molten materials 4, 5, 6, 9, and 10, which contains 1.5 mass% or more and 14.0 mass% or less of Si, 0.010 mass% or more and 1.5 mass% or less of Ti, with the remainder being Al and unavoidable impurities, by any one of manufacturing methods A to C, which control the manufacturing conditions of casting, homogenization treatment, and rolling. As a result, the RD-TD parallel plane of the molten material is 10,000 μm 2 In the observation field, the distribution of coarse intermetallic compounds containing Ti, each having an equivalent circle diameter of 10.00 μm or more, is controlled to be less than 5 particles. The melted member (second plate material) is made from any of the melted materials 4 to 6, which contain 0.010 mass% to 0.5 mass% of V, with the remainder consisting of Al and inevitable impurities, by one of the manufacturing methods a to c, in which the manufacturing conditions of the homogenization treatment and rolling are controlled. As a result, the RD-TD parallel plane of the melted member (second plate material) is 10,000 μm 2 In the observation field, 10 or more fine intermetallic compounds containing V and having a circle equivalent diameter of 0.01 μm or more and less than 5.00 μm are densely distributed. In the erosion resistance test, it was confirmed that the erosion of the melted material (second plate material) by the molten solder was reduced by allowing the Ti in the molten solder melted by the melting material (first plate material) to react sufficiently with the V in the melted material (second plate material) to form a high-melting point compound.

[0124] Sample 41 differs from Samples 17 to 19 in that the melting member (the brazing filler metal for the first plate) uses melting material 11 further containing Zn in the range of 0.01 mass % to 5.0 mass %. The melting member (the brazing filler metal for the first plate) is produced by manufacturing method A, in which the manufacturing conditions of casting, homogenization treatment, and rolling are controlled. The melted member (the second plate) is also produced by manufacturing method A, in which the manufacturing conditions of homogenization treatment and rolling are controlled. In a test of the erosion resistance of Sample 41, it was confirmed that the erosion of the member to be fused (second plate material) by the molten brazing filler metal was reduced.

[0125] Sample 11 is a V-melt type. The molten material 1 (the brazing filler metal for the first plate material) contains 1.5 to 14.0 mass% Si, 0.010 to 1.5 mass% V, and the remainder being Al and unavoidable impurities, and is produced by manufacturing method A, which controls the manufacturing conditions of casting, homogenization, and rolling. In the RD-TD parallel plane of the molten material, the distribution of coarse intermetallic compounds containing V is controlled to less than 5. In addition, the melted member (second plate material) is made by manufacturing method a in which the melted material 17 has a Ti content of 0.005 mass%, which is outside the range of 0.010 mass% or more and 0.5 mass% or less, and the manufacturing conditions of homogenization treatment and rolling are controlled, and the number of fine intermetallic compounds in the melted member (second plate material) is less than 10. In the erosion resistance test of this sample 11, the number of fine intermetallic compounds in the melted member (second plate material) was small, and there was no effect in reducing the erosion of the melted member (second plate material) by the molten brazing filler metal.

[0126] Sample 35 is a V-fusion type. The molten material (the brazing filler metal for the first plate material) contains 1.5 mass % or more and 14.0 mass % or less of Si, but the V content is 0.005 mass % or less, which is outside the range of 0.010 mass % or more and 1.5 mass % or less, and is produced by manufacturing method A, which controls the manufacturing conditions of casting, homogenization treatment, and rolling, from molten material 16. The number of coarse intermetallic compounds in the molten material (the brazing filler metal for the first plate material) is less than five. The melted member (second plate material) contains 0.010 mass% or more and 0.5 mass% or less of Ti, with the remainder being Al and unavoidable impurities, and is produced by manufacturing method a, in which the manufacturing conditions of homogenization treatment and rolling are controlled. The melted member (second plate material) has 10 or more fine intermetallic compounds. In the erosion resistance test of sample 35, the V content of the molten material (the brazing material of the first plate material) was 0.005 mass%, which was below the lower limit, so there was no effect in reducing erosion of the material to be melted (the second plate material) by the molten brazing material.

[0127] Samples 49 to 52 are V-fusion type. The molten material (brazing filler metal for the first plate material) contains 1.5 mass% or more and 14.0 mass% or less of Si, 0.010 mass% or more and 1.5 mass% or less of V, with the remainder being Al and unavoidable impurities, and is produced by any of manufacturing methods D to G in which the molten material 1 is performed without controlling any of the manufacturing conditions of casting, homogenization treatment, or rolling. The number of coarse intermetallic compounds in the molten material (brazing filler metal for the first plate material) exceeded five. The melted member (second plate material) contains 0.010 mass% or more and 0.5 mass% or less of Ti, with the remainder being Al and unavoidable impurities, and is produced by manufacturing method a, in which the manufacturing conditions of homogenization treatment and rolling are controlled. The melted member (second plate material) has 10 or more fine intermetallic compounds. In the erosion resistance test of samples 49 to 52, the number of coarse intermetallic compounds in the molten component (the brazing filler metal of the first plate material) was large, and there was no effect in reducing the erosion of the molten component (the second plate material) by the molten brazing filler metal.

[0128] Samples 55 to 57 are V-fusion type. The molten material (the brazing filler metal for the first plate material) contains 1.5 to 14.0 mass% Si, 0.010 to 1.5 mass% V, and the remainder being Al and unavoidable impurities. The molten material 1 is produced by manufacturing method A, which controls the manufacturing conditions of casting, homogenization, and rolling. The distribution of coarse intermetallic compounds is controlled to less than 5. The melted member (second plate material) contains 0.010 mass% or more and 0.5 mass% or less of Ti, with the remainder being Al and unavoidable impurities, and is produced by any of manufacturing methods d to f, in which the melted material 1 is performed without controlling either the homogenization treatment or the rolling manufacturing conditions. The melted member (second plate material) has less than 10 fine intermetallic compounds. In the erosion resistance test of samples 55 to 57, the number of fine intermetallic compounds in the melted material (second plate material) was small, and there was no effect in reducing the erosion of the melted material (second plate material) by the molten brazing filler metal.

[0129] Sample 45 was a combination in which both the melting member (the brazing filler metal of the first plate material) and the melted member (the second plate material) contained V, but neither contained Ti, so it was ineffective in reducing erosion.

[0130] Sample 24 is a Ti fusion type. The molten material 4 (the brazing filler metal for the first plate material) contains 1.5 to 14.0 mass% Si, 0.010 to 1.5 mass% Ti, and the remainder being Al and unavoidable impurities, and is produced by manufacturing method A, which controls the manufacturing conditions of casting, homogenization, and rolling. In the RD-TD parallel plane of the molten material, the distribution of coarse intermetallic compounds containing Ti is controlled to less than 5 particles. In addition, the melted member (second plate material) is made by manufacturing method a in which the melted material 19 has a V content of 0.005 mass%, which is outside the range of 0.010 mass% or more and 0.5 mass% or less, and the manufacturing conditions of homogenization treatment and rolling are controlled, and the number of fine intermetallic compounds in the melted member (second plate material) is less than 10. In the erosion resistance test of sample 24, the number of fine intermetallic compounds in the melted material (second plate material) was small, and there was no effect in reducing the erosion of the melted material (second plate material) by the molten brazing filler metal.

[0131] Sample 43 is a Ti fusion type. The molten material (the brazing filler metal for the first plate material) contains 1.5 mass% or more and 14.0 mass% or less of Si, but the Ti content is 0.005 mass% which is outside the range of 0.010 mass% or more and 1.5 mass% or less, and is produced by manufacturing method A in which the manufacturing conditions of casting, homogenizing treatment, and rolling are controlled for molten material 18. The number of coarse intermetallic compounds in the molten material (the brazing filler metal for the first plate material) is less than five. The melted member (second plate material) contains 0.010 mass % or more and 0.5 mass % or less of V, with the remainder being Al and unavoidable impurities, and is produced by manufacturing method a, in which the manufacturing conditions of homogenization treatment and rolling are controlled. The number of fine intermetallic compounds in the melted member (second plate material) is 10 or more. In the erosion resistance test of sample 43, the Ti content of the molten material (the brazing material of the first plate material) was 0.005 mass%, which was below the lower limit, so there was no effect in reducing erosion of the molten material (the second plate material) by the molten brazing material.

[0132] Samples 60 to 63 are Ti fusion type. The molten material (brazing filler metal for the first plate material) contains 1.5 mass% or more and 14.0 mass% or less of Si, 0.010 mass% or more and 1.5 mass% or less of Ti, and the remainder is Al and unavoidable impurities. The molten material 4 is produced by any of manufacturing methods D to G, in which the manufacturing conditions of casting, homogenization treatment, or rolling are not controlled. The number of coarse intermetallic compounds in the molten material (brazing filler metal for the first plate material) exceeded five. The melted member (second plate material) contains 0.010 mass % or more and 0.5 mass % or less of V, with the remainder being Al and unavoidable impurities, and is produced by manufacturing method a, in which the manufacturing conditions of homogenization treatment and rolling are controlled. The melted member (second plate material) has 10 or more fine intermetallic compounds. In the erosion resistance test of samples 60 to 63, the number of coarse intermetallic compounds in the molten material (the brazing material of the first plate material) was large, and there was no effect in reducing the erosion of the molten material (the second plate material) by the molten brazing material.

[0133] Samples 66 to 68 are Ti fusion type. The molten material (the brazing filler metal for the first plate material) contains 1.5 to 14.0 mass% Si, 0.010 to 1.5 mass% Ti, and the remainder being Al and unavoidable impurities. The molten material 4 is produced by manufacturing method A, which controls the manufacturing conditions of casting, homogenization, and rolling. The distribution of coarse intermetallic compounds is controlled to less than 5. The melted member (second plate material) contains 0.010 mass % or more and 0.5 mass % or less of V, with the remainder being Al and unavoidable impurities, and is produced by any of manufacturing methods d to f, in which the melted material 4 is performed without controlling either the homogenization treatment or the rolling manufacturing conditions. The melted member (second plate material) has less than 10 fine intermetallic compounds. In the erosion resistance test of samples 66 to 68, the number of fine intermetallic compounds in the melted material (second plate material) was small, and there was no effect in reducing the erosion of the melted material (second plate material) by the molten brazing filler metal.

[0134] Sample 46 was a combination in which both the melting member (the brazing filler metal of the first plate material) and the melted member (the second plate material) contained Ti, but neither contained V, so it was ineffective in reducing erosion.

[0135] In Samples 32 and 42, the brazing filler metal of the first plate material contained neither V nor Ti, and the second member contained 0.010 mass % or more and 0.5 mass % or less of V or Ti. In the erosion resistance test of Samples 32 and 42, it was not possible to reduce the erosion of the member to be fused (second plate material) by the molten brazing filler metal.

[0136] Since it was not possible to manufacture a meltable component for sample 12, the erosion resistance test was not performed. Table 5 lists this as "Cannot manufacture meltable component." Sample 33 was not tested for erosion resistance due to insufficient brazing filler, and is listed in Table 5 as "Brazed NG." As it was not possible to produce fusion parts for Samples 34 and 36, the erosion resistance test was not performed. Table 5 lists these as "Fusion part production not possible." [Example]

[0137] A first plate material clad with brazing material on one side and a second plate material consisting of a single layer were produced using different materials and manufacturing conditions. A first member cut out from the first plate material was assembled to a second member cut out from the second plate material, and the assembly was subjected to a heat treatment equivalent to brazing. The tensile strength Rm of the second member after this heat treatment was evaluated.

[0138] (material) A. Materials for melting components The combination of the first plate material and the second plate material was [Melting V-Melted Ti Type] or [Melting Ti-Melted V Type], and in Example 2, Melting Material 1 in Table 1 was used as the material for the melting member of [Melting V-Melted Ti Type], and in Example 2, Melting Material 4 in Table 1 was used as the material for the melting member of [Melting Ti-Melted V Type].

[0139] B. Material of the melted part The material for the melted member of [Melting V - Ti melted type] (ingot: hereinafter referred to as the melted material) contains 0.010% by mass to 0.5% by mass of Ti, and further contains Mn, Si, Fe, and Cu. In addition to Ti, Mn, Si, Fe, and Cu, it also contains Zn.

[0140] Specifically, the material to be melted 7 contains 0.10 mass % to 2.0 mass % of Mn, 0.05 mass % to 1.5 mass % of Si, 0.05 mass % to 1.0 mass % of Fe, and 0.010 mass % to 2.0 mass % of Cu. The materials 11 and 12 to be melted contain 0.10 mass% or more and 2.0 mass% or less of Mn, 0.05 mass% or more and 1.5 mass% or less of Si, 0.05 mass% or more and 1.0 mass% or less of Fe, 0.010 mass% or more and 2.0 mass% or less of Cu, and 0.01 mass% or more and 1.0 mass% or less of Mg. The material to be melted 13 contains 0.10 mass% to 2.0 mass% Mn, 0.05 mass% to 1.5 mass% Si, 0.05 mass% to 1.0 mass% Fe, 0.010 mass% to 2.0 mass% Cu, and 0.01 mass% to 5.0 mass% Zn. The material to be melted 15 contains 0.10% by mass or more and 2.0% by mass or less of Mn, 0.05% by mass or more and 1.5% by mass or less of Si, 0.05% by mass or more and 1.0% by mass or less of Fe, 0.010% by mass or more and 2.0% by mass or less of Cu, 0.01% by mass or more and 0.35% by mass or less of Cr, 0.01% by mass or more and 0.35% by mass or less of Zr, and 0.01% by mass or more and 1.0% by mass or less of Sr. The materials 8, 21, 22, 24, and 25 to be melted have a Mn content outside the range of 0.10 mass% or more and 2.0 mass% or less, a Cu content outside the range of 0.010 mass% or more and 2.0 mass% or less, or an Fe content outside the range of 0.05 mass% or more and 1.5 mass% or less.

[0141] The material to be melted of the melted member of [Melted Ti - Melted V-type] contains 0.010% by mass to 0.5% by mass of V, and further contains Mn, Si, Fe, and Cu. In addition to Ti, Mn, Si, Fe, and Cu, it also contains one or a combination of Mg, Zn, Cr, Zr, and Sr.

[0142] Specifically, the materials 9 and 10 to be melted contain 0.10 to 2.0 mass % of Mn, 0.05 to 1.5 mass % of Si, 0.05 to 1.0 mass % of Fe, and 0.010 to 2.0 mass % of Cu. The material to be melted 14 contains 0.10 mass% to 2.0 mass% Mn, 0.05 mass% to 1.5 mass% Si, 0.05 mass% to 1.0 mass% Fe, 0.010 mass% to 2.0 mass% Cu, and 0.01 mass% to 1.0 mass% Mg. The material to be melted 23 has a Si content outside the range of 0.05 mass % or more and 1.5 mass % or less.

[0143] The compositions of the materials to be melted 7 to 16 and 21 to 25 are shown in Table 6. The remainder of the materials to be melted 7 to 16 and 21 to 25, which is not shown in Table 6, is aluminum and inevitable impurities.

[0144] [Table 6]

[0145] A first plate material was produced using a material (either melting material 1 or 4) under manufacturing conditions (manufacturing method A), and a second plate material was produced using a material (either melting material 7-16, 21-25) under manufacturing conditions (manufacturing method a). A first member cut out from the first plate material was assembled to a second member cut out from the second plate material to form assemblies called samples 4-10, 13-16, 20-23, and 26. Samples 4-10, 13-16, 20-23, and 26 were subjected to heat treatment equivalent to brazing, and the strength of the second plate material of each of samples 4-10, 13-16, 20-23, and 26 after the heat treatment was measured.

[0146] The conditions for the heat treatment equivalent to brazing were heating to 600°C at an average heating rate of 100°C / min, holding at 600°C for 3 minutes, then cooling to 150°C at a cooling rate of 100°C / min, and then air-cooling to room temperature. During this heat treatment, the assembly was exposed to nitrogen gas in a heating furnace, with the nitrogen gas supply rate being 150 liters / min. After the heat treatment, samples were cut out parallel to the rolling direction from the second members of each of Samples 4 to 10, 13 to 16, 20 to 23, and 26 to prepare No. 13B test pieces according to the tensile testing method for metallic materials (JIS Z2241:2011), and the tensile strength Rm was measured.

[0147] A tensile strength Rm of 150 MPa or more was judged as good, 120 MPa or more and less than 150 MPa as fair or good, and these were also judged as pass, and less than 120 MPa was judged as poor (fail).

[0148] Table 7 shows the tensile strength Rm of each sample, with good being A, fairly good being B, and poor being C. Table 7 also shows the measurement of the chemical compounds of each sample before the heat treatment equivalent to brazing, which was performed in Example 1, and the evaluation of erosion resistance after the heat treatment equivalent to brazing was performed on each sample.

[0149] [Table 7]

[0150] The second members of Samples 4 to 10 and 20 to 23 had good or slightly good tensile strength Rm. Of these, Samples 4 to 9 and 20 to 22 also had good erosion resistance, while Samples 10 and 23 had poor erosion resistance.

[0151] Samples 13, 16, and 26 had poor tensile strength Rm because the Mn content was outside the range of 0.10 mass% or more and 2.0 mass% or less, the Si content was outside the range of 0.05 mass% or more and 1.5 mass% or less, or the Cu content was outside the range of 0.010 mass% or more and 2.0 mass% or less.

[0152] Furthermore, for sample 14, an attempt was made to manufacture melt material 22 by manufacturing method a, but manufacturing was not possible. Table 7 shows this as "Meltable material manufacturing NG." Sample 15 had an Fe content of less than 0.05 mass%, which would have increased costs, so manufacturing was not attempted (Table 7 shows this as "Meltable material cost NG"). [Example]

[0153] A first plate material clad with a brazing material on one side and an extruded material made of a melted material were produced using different materials and manufacturing conditions, and a first member cut out from the first plate material was assembled to a second member cut out from the extruded material, and a heat treatment equivalent to brazing was performed, and the erosion caused by the brazing material of the first member on the second member was evaluated.

[0154] (material) A. Materials for melting components In Example 3, either melt material 1 or melt material 4 in Table 1 was used as the material of the melt member.

[0155] B. Material of the melted part In Example 3, any one of meltable material 1 in Table 2, meltable material 4 in Table 2, and meltable material 7 in Table 6 was used as the material of the meltable member.

[0156] (Method of manufacturing the first plate material) The first plate material of Example 3 was manufactured by Manufacturing Method A in Table 3, which consists of a brazing material manufacturing process and a clad material manufacturing process, similar to the manufacturing method of the first plate material of Example 1, and controls the manufacturing conditions of casting, homogenization treatment, and rolling.

[0157] (Manufacturing method of extruded material) The manufacturing method for extruded material includes a homogenization process in which an ingot for the extruded material is homogenized, and an extrusion process in which the ingot is extruded. In this manufacturing method, the manufacturing conditions are the heating temperature in the homogenization process and the extrusion temperature and extrusion speed in the extrusion process. Table 8 shows the manufacturing conditions for the manufacturing method for extruded material. Hereinafter, the manufacturing methods for extruded material will be designated by the symbol "Ext" to distinguish them from the other manufacturing methods A to G and a to f.

[0158] [Table 8]

[0159] A first plate was produced using the material (either melt material 1 or 4) under manufacturing conditions (Manufacturing method A in Table 3), and an extruded material was produced using the material (either melted material 1, 4, or 7) under manufacturing conditions (Manufacturing method Ext in Table 8). A first member cut out from the first plate was assembled with a second member cut out from the extruded material to produce assemblies called samples 69 to 73. Samples 69 to 73 were subjected to a heat treatment equivalent to brazing, and the erosion resistance of samples 69 to 73 was evaluated. Before the heat treatment was performed on samples 69 to 73, the compounds of the first and second members constituting samples 69 to 73 were measured.

[0160] The first member was prepared by cutting out a first plate material into a size of 60 mm in length and 60 mm in width, similar to the first member of Example 1.

[0161] A tube was prepared as the extruded material. This tube was flattened, with a cross-sectional dimension perpendicular to the extrusion direction of 32 mm in width and an overall thickness of 3.5 mm, with each part being 1.0 mm thick. A plate piece measuring 60 mm in the extrusion direction and 32 mm in the direction perpendicular to the extrusion direction was cut out from the flat part of this extruded material, and this was used as the second component.

[0162] The evaluation of erosion resistance, the measurement of coarse intermetallic compounds in the first member, and the measurement of fine intermetallic compounds in the second member were performed according to the procedures for the evaluation of erosion resistance, the measurement of coarse intermetallic compounds in the first member, and the measurement of fine intermetallic compounds in the second member in Example 1. A sample piece cut out from the second member was mechanically polished and electrolytically polished to prepare a thin film, and a 10,000 μm diameter cross section of the ED-TD parallel plane was measured using a TEM (transmission electron microscope). 2 The observation field was set to 100 μm square and minute intermetallic compounds were measured.

[0163] Table 9 shows the number of coarse compounds measured in the melted member, the number of fine compounds measured in the melted member (second member) for Samples 69 to 73, and the evaluation of erosion resistance.

[0164] [Table 9]

[0165] Samples 69 and 71 are V-melt types. The molten material 1 (the brazing filler metal for the first plate material) contains 1.5 mass % or more and 14.0 mass % or less of Si, 0.010 mass % or more and 1.5 mass % or less of V, and the remainder is Al and unavoidable impurities. The molten material 1 is produced by manufacturing method A, which controls the manufacturing conditions of casting, homogenization treatment, and rolling. As a result, the RD-TD parallel plane of the molten material is 10,000 μm 2 In the observation field, the distribution of coarse intermetallic compounds containing V, each having an equivalent circle diameter of 10.00 μm or more, is controlled to less than 5 particles. The melted member (second member) is made from either melted material 1 or 7, which contains 0.010 mass % or more and 0.5 mass % or less of Ti, with the remainder consisting of Al and inevitable impurities, by a manufacturing method Ext, which controls the manufacturing conditions of the homogenization treatment, extrusion temperature and extrusion speed in the extrusion process. As a result, the ED-TD parallel plane of the melted member (second member) is 10,000 μm 2 In the observation field, 10 or more fine intermetallic compounds containing Ti and having a circle equivalent diameter of 0.01 μm or more and less than 5.00 μm are densely distributed. In the erosion resistance test, it was confirmed that the erosion of the melted material (second material) by the molten solder was reduced by allowing the V in the molten solder melted by the melting material (first plate material) to react sufficiently with the Ti in the melted material (second material) to form a high-melting point compound.

[0166] Sample 70 is a Ti fusion type. The molten material 4 (the brazing filler metal for the first plate material) contains 1.5 mass % or more and 14.0 mass % or less of Si, 0.010 mass % or more and 1.5 mass % or less of Ti, and the remainder is Al and unavoidable impurities. The molten material 4 is produced by manufacturing method A, which controls the manufacturing conditions of casting, homogenization treatment, and rolling. As a result, the RD-TD parallel plane of the molten material is 10,000 μm 2 In the observation field, the distribution of coarse intermetallic compounds containing Ti, each having an equivalent circle diameter of 10.00 μm or more, is controlled to be less than 5 particles. The melted material 4 contains 0.010 mass % or more and 0.5 mass % or less of V, with the remainder consisting of Al and inevitable impurities, and is produced by a manufacturing method Ext in which the manufacturing conditions of the homogenization treatment, extrusion temperature and extrusion speed in the extrusion process are controlled. As a result, the ED-TD parallel plane of the melted material (second member) is 10,000 μm 2 In the observation field, 10 or more fine intermetallic compounds containing V and having a circle equivalent diameter of 0.01 μm or more and less than 5.00 μm are densely distributed. In the erosion resistance test, it was confirmed that the erosion of the melted material (second material) by the molten solder was reduced by allowing the Ti in the molten solder melted by the melting material (first plate material) to react sufficiently with the V in the melted material (second material) to form a high-melting point compound.

[0167] In sample 72, the number of coarse compounds in the melting component (the brazing filler metal of the first plate material) was less than 5, and the number of fine compounds in the melted component (the second component) was 10 or more. However, regardless of the distribution of these compounds, the combination of the melting component (the brazing filler metal of the first plate material) and the melted component (the second component) both contained V, but neither contained Ti, so there was no effect in reducing erosion.

[0168] Sample 73 was a combination in which both the melting component (the brazing filler metal of the first plate material) and the melted component (the second component) contained Ti, but neither contained V, so it was ineffective in reducing erosion. [Explanation of symbols]

[0169] 1 Heat exchanger (brazed product) 2 Tube (second component) 3 Fins 4,5 Header (first member)

Claims

1. An assembly for brazing heat treatment comprising a first member and a second member assembled with the first member, The first member includes a core material and a brazing material made of a molten material clad on one or both sides of the core material directly or via an intermediate layer, the second member includes at least a substrate made of a member to be melted, The melted material contains 1.5 mass% or more and 14.0 mass% or less of Si, 0.010 mass% or more and 1.5 mass% or less of one of V and Ti, and the balance being Al and inevitable impurities, The melted member contains 0.010 mass % or more and 0.5 mass % or less of the other of V and Ti, with the remainder being Al and inevitable impurities, The RD-TD parallel plane of the melting member is 10000 μm ２ In the observation field of The RD-TD parallel plane or ED-TD parallel plane of the melted material is 10,000 μm ２ 1. An assembly for brazing heat treatment, characterized in that, in an observation field of the above, there are 10 or more intermetallic compounds having a circle equivalent diameter of 0.01 μm or more and less than 5.00 μm and containing the other.

2. 2. The assembly for brazing heat treatment according to claim 1, wherein the melted member further contains any one of the following additional elements 1 to 4 or any combination of a plurality of these additional elements: Additional element 1: Mn, Si, Fe, and Cu, in which the Mn content is 0.10 mass% or more and 2.0 mass% or less, the Si content is 0.05 mass% or more and 1.5 mass% or less, the Fe content is 0.05 mass% or more and 1.0 mass% or less, and the Cu content is 0.010 mass% or more and 2.0 mass% or less. Additional element 2: Mg, and the Mg content is 0.01 mass % or more and 1.0 mass % or less. Additional element 3: Zn, and the Zn content is 0.01 mass % or more and 5.0 mass % or less. Additional element 4: Any one or any combination of Cr, Zr, and Sr, wherein the Cr content is 0.01 mass% or more and 0.35 mass% or less, the Zr content is 0.01 mass% or more and 0.35 mass% or less, and the Sr content is 0.01 mass% or more and 1.0 mass% or less.

3. 3. The assembly for brazing heat treatment according to claim 1, wherein the melting member further contains 0.01% by mass or more and 5.0% by mass or less of Zn.

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