An interface stress treatment method for aluminum-iron composite material and aluminum-iron composite material

Abstract

The present application belongs to the field of metallurgy, and particularly relates to a kind of aluminum-iron composite material interface stress treatment methods, comprising the following steps: S1, the surface of iron base material is activated and is handled;S2, the first aluminum material is used to the iron base material and is hot-dipped, the second aluminum material is used to the iron base material after hot-dipping and is cast, and the aluminum-iron composite material is obtained, the first aluminum material is 770-790 DEG C molten aluminum material, and the second aluminum material is 700-720 DEG C molten aluminum material;S3, the aluminum-iron composite material is heated to 280-320 DEG C at a heating rate of 3-5 DEG C / min, and is kept for 2.5-3.5h;The present application is heated to a certain temperature and time by heat treatment to the aluminum-iron composite material obtained by casting, so as to achieve the effect of reducing the interfacial stress of aluminum-iron composite material bimetal, weaken the stress of aluminum side in liquid-solid composite aluminum / iron bimetal, can guarantee the metallurgical bonding integrity of aluminum / iron bimetal interface, and improve the shear strength of aluminum / iron bimetal.

Description

TECHNICAL FIELD

[0001] The application belongs to the technical field of metallurgy, and particularly relates to an aluminum-iron composite material interface stress treatment method and an aluminum-iron composite material. BACKGROUND

[0002] With the increasing demand for energy saving and emission reduction, the lightweight of key components (engines) of automobiles becomes a key object of research, and an aluminum / iron liquid-solid composite casting method is adopted, a reaction layer is formed between aluminum and iron, metallurgical bonding is generated, and the low density, lightweight, corrosion resistance of aluminum alloy and the excellent strength, wear resistance, excellent vibration damping and yield strength of cast iron material are combined.

[0003] The working environment of an automobile engine is harsh, and high pressure and high heat have requirements for the performance of aluminum / iron bimetallic materials, but cracking defects may occur at the bimetallic interface, which is caused by the intermetallic compound generated at the interface of aluminum-iron metallurgical bonding being a hard and brittle phase, and by the internal stress caused by the difference in thermal expansion coefficients of aluminum and iron; these factors may cause cracking defects at the aluminum-iron bonding interface, which is not conducive to the service life of the engine in harsh environments.

[0004] In view of these factors, the conventional way for aluminum / iron bimetallic bonding is to reduce the adverse phase and add an iron-based interlayer to inhibit cracking, such as using metal mold casting to accelerate cooling to reduce element diffusion; and using zinc and copper plating on the surface of the iron-based substrate to promote metallurgical reaction and change the composition of the hard and brittle phase and improve the interface stress.

[0005] The liquid-solid aluminum-iron composite method of metal mold casting can accelerate the solidification and cooling speed of the aluminum liquid, thereby slowing down the formation of the aluminum-iron interface adverse phase, but too fast cooling may increase the aluminum-iron interface stress at a certain angle, leading to cracking. Although the introduction of the iron-based interlayer on the surface of the substrate improves the aluminum-iron metallurgical bonding, the effect on improving the interface stress is weak. SUMMARY

[0006] To solve the above technical problems, the application provides an aluminum-iron composite material interface stress treatment method, which comprises the following steps: S1, activating the surface of the iron-based substrate; S2, using a first aluminum material to hot dip the iron-based substrate, and using a second aluminum material to cast the hot-dipped iron-based substrate to obtain the aluminum-iron composite material, the first aluminum material being a molten aluminum material at 770-790 DEG C, and the second aluminum material being a molten aluminum material at 700-720 DEG C; S3, heating the aluminum-iron composite material to 280-320 DEG C at a heating rate of 3-5 DEG C / min, and keeping the temperature for 2.5-3.5 h.

[0007] In the step S1, the activation treatment comprises grinding, alkali washing and acid washing.

[0008] The iron base material is iron or steel in the step S1, and the first aluminum material and the second aluminum material are aluminum or aluminum alloy in the step S2.

[0009] The iron base material is preheated before the step S2.

[0010] The preheating is to heat the iron base material to 340-360 DEG C at a temperature of 500-600 DEG C for 2-3 min.

[0011] Further, the iron base material is heated to 340, 345 DEG C, 350 DEG C, 355 DEG C, 360 DEG C, or a range between any one or two of them, the first aluminum material is molten aluminum material with a temperature in a range between any one or two of 770 DEG C, 775 DEG C, 780 DEG C, 785 DEG C, 790 DEG C, and the second aluminum material is molten aluminum material with a temperature in a range between 700 DEG C, 705 DEG C, 710 DEG C, 715 DEG C, 720 DEG C.

[0012] The step S3 further comprises: S31, heating the aluminum-iron composite material to 280-320 DEG C at a heating rate of 3-5 DEG C / min, and holding for 2.5-3.5 h; and S32, furnace cooling the aluminum-iron composite material.

[0013] Further, the heating rate is any one or a range between any two of 3 DEG C / min, 4 DEG C / min, 5 DEG C / min, the holding time is any one or a range between any two of 2.5 h, 3 h, 3.5 h, and S32, furnace cooling the aluminum-iron composite material.

[0014] The aluminum-iron composite material comprises an aluminum plating layer, the aluminum plating layer comprises a metallurgical reaction layer and a hot-dip melt layer, the metallurgical reaction layer comprises Al5Fe2, Al 13 Fe4, the metallurgical reaction layer has a thickness of 4-6 mu m, and the aluminum plating layer has a thickness of 10-14 mu m.

[0015] To solve the above technical problems, the application further provides an aluminum-iron composite material prepared by the aluminum-iron composite material interface stress treatment method.

[0016] The present application controls the temperature when the iron base material is hot-dipped, and the aluminum-iron composite material obtained by casting is heat-treated at a certain temperature and time, so as to reduce the intermetallic interface stress of the aluminum-iron composite material, on the one hand, the stress on the aluminum side in the liquid-solid composite aluminum / iron bimetal can be weakened, the metallurgical combination integrity of the aluminum / iron bimetal interface can be ensured, and the shear strength of the aluminum / iron bimetal can be improved; on the other hand, after the residual stress of the aluminum / iron bimetal is released, the original aluminum / iron bimetal as-cast sample can be processed more freely and more selectively, and the aluminum / iron bimetal interface is ensured to be complete after processing. BRIEF DESCRIPTION OF DRAWINGS

[0017] In order to more clearly illustrate the technical solutions in the embodiments of the present application or the prior art, the following will briefly introduce the drawings needed to be used in the embodiments or the prior art description. Obviously, the drawings in the following description only constitute some embodiments of the present application, and for those skilled in the art, other drawings can also be obtained according to the structures shown in the drawings without creative labor.

[0018] Figure 1 Micrographs of the aluminum-iron composite materials after heat treatment in Example 1, Comparative Example 4 and Comparative Example 5 of the present application;

[0019] Figure 2 XRD stress diagram of the aluminum-iron composite material after heat treatment in Example 1 of the present application;

[0020] Figure 3 Micrographs of the aluminum-iron composite material in Comparative Example 1 of the present application;

[0021] Figure 4 XRD stress diagram of the aluminum-iron composite material in Comparative Example 1 of the present application;

[0022] Figure 5 Actual physical diagram and micrograph of the aluminum-iron composite material after cutting in Comparative Example 1 of the present application;

[0023] Figure 6 Micrographs of the aluminum-iron composite materials in Comparative Example 2 and Comparative Example 3 of the present application;

[0024] Figure 7 Micrographs of the aluminum-iron composite materials without heat treatment in Comparative Example 1, Comparative Example 2 and Comparative Example 3 of the present application.

[0025] The implementation, functional features and advantages of the present application will be further described with reference to the embodiments and the accompanying drawings. DETAILED DESCRIPTION

[0026] The technical solutions in the embodiments will be described clearly and completely below. Obviously, the described embodiments are only a part of, rather than all of, the embodiments of the present application. Based on the embodiments in the present application, all other embodiments obtained by a person of ordinary skill in the art without creative effort belong to the protection scope of the present application.

[0027] The present application provides a method for reducing residual internal stress of aluminum / iron bimetallic composite material interface, which overcomes the problem of easy cracking of aluminum / iron bimetallic composite material interface in the prior art. By controlling the hot dipping temperature of the iron base material and through slow heating, holding and slow cooling, the internal stress of the interface structure of the bimetallic material is reduced, which can effectively solve the problem of easy cracking of the interface, so as to realize the stability of the interface bonding of the aluminum / iron bimetallic composite material. The specific steps are as follows:

[0028] S1, activating the surface of the iron base material;

[0029] In the embodiments of the present application, the iron base material is nodular cast iron QT500, which has high tensile strength, yield strength and elastic modulus. The composition is C: 3.6wt%-3.8wt%, Si: 2.5wt%-2.9wt%, Mn<0.6wt%, S<0.025wt%, P<0.08wt%, Mg: 0.03wt%-0.05wt%, RE: 0.03wt%-0.05wt%, and the balance is Fe and unavoidable impurities.

[0030] In the embodiments of the present application, the step of activating the surface of the iron base material is as follows: sandpaper is used to polish the surface of the iron base material to 1000 mesh to ensure that the surface is smooth and flat; the iron base material is ultrasonically washed in a 10wt% NaOH solution for 5 minutes to remove oil stains on the surface of the base material, and then the residual alkali solution on the surface of the base material is washed off with running water; the iron base material is placed in a 10wt% HCl solution and ultrasonically washed for 5 minutes to further remove surface rust; the iron base material is placed in alcohol and ultrasonically washed for 10 seconds and then dried to prevent rusting.

[0031] S2, using a first aluminum material to hot dip the iron base material, and using a second aluminum material to cast the iron base material after hot dipping to obtain the aluminum-iron composite material, the first aluminum material being a molten aluminum material at 770-790℃, and the second aluminum material being a molten aluminum material at 700-720℃;

[0032] In the embodiments of the present application, the S2 step adopts the following processing method: two portions of aluminum alloy are melted by a silicon-carbon rod furnace, the aluminum alloy is melted at 730 DEG C, the molten aluminum alloy is degassed and temperature-adjusted at 730 DEG C by using hexachloroethane, one portion of the aluminum alloy is temperature-adjusted to 700-720 DEG C as a casting melt, the temperature is stabilized at 710 DEG C for 20 min, the metal mold and other tools that will contact the melt are coated with boron nitride, the mold is preheated in a 200 DEG C electric heating constant temperature air drying machine, and the other portion of the aluminum alloy is temperature-adjusted to 770-790 DEG C as a hot-dipping melt, the temperature is stabilized at 780 DEG C for 20 min.

[0033] In the embodiments of the present application, the aluminum alloy is selected as Al-Si alloy ZL702A which has good fluidity and excellent performance. The composition of the Al-Si alloy ZL702A is as follows: Si: 6.0wt%-8.0wt%, Mg: 0.25wt%-0.50wt%, Cu: 1.2wt%-1.8wt%, Mn: 0.1wt%-0.25wt%, Ti: 0.1wt%-0.2wt%, Fe≤0.15wt%, Sr: 0.01wt%-0.06wt%, and the balance is Fe and inevitable impurities. The inventors find through research that hot-dipping of the iron-based material by using the molten aluminum material at 770-790 DEG C can obtain the iron-based material with a complete metallurgical reaction layer, and in order to prevent the aluminum-iron composite material from being weakened in performance due to the over-thickness of the intermediate layer between the aluminum material and the iron-based material, a higher temperature is not used for hot-dipping.

[0034] In the step S2, the residual stress of the aluminum side of the aluminum-iron composite material is 60-90 MPa.

[0035] S3, performing heat treatment on the aluminum-iron composite material.

[0036] In the embodiments of the present application, the aluminum-iron composite material obtained by casting is subjected to heat treatment at a certain temperature and for a certain time, so as to achieve the effect of reducing the bimetal interface stress of the aluminum-iron composite material, which on the one hand weakens the stress of the aluminum side in the liquid-solid composite aluminum / iron bimetal, can ensure the metallurgical bonding integrity of the aluminum / iron bimetal interface, and improve the shear strength of the aluminum / iron bimetal.

[0037] In the step S3, the residual stress of the aluminum side of the aluminum-iron composite material is between 12-18 MPa.

[0038] Further, the shear strength of the aluminum-iron composite material is tested to be 15-35 MPa.

[0039] Further, the average microhardness of the aluminum-iron composite material is tested to be 75-90 HV (Vickers hardness), and the average microhardness is the average hardness of the aluminum within a range of 1 cm at the interface of the aluminum-iron composite material.

[0040] The technical solutions of the present application are further described below in combination with specific examples.

[0041] Example 1

[0042] The activated iron matrix was kept in a ceramic fiber heat treatment furnace at 550℃ for 2 minutes and 50 seconds to 350℃; the preheated iron matrix was hot-dipped in an aluminum alloy melt at 780℃ for 3 minutes; the hot-dipped iron matrix was clamped into a mold at 200℃ and fixed, and an aluminum alloy melt at 710℃ was poured in 5 seconds to obtain an aluminum-iron composite material; a ceramic fiber furnace was selected as the heat treatment furnace, the aluminum-iron composite material was cooled to room temperature, and then heated to the target temperature at a heating rate of 5℃ / min in the heat treatment furnace, kept at 300℃ for 3h, and then slowly furnace-cooled to obtain a treated aluminum-iron composite material, which was subjected to shear strength testing and microhardness testing, and the shear strength was 30.2MPa and the average microhardness was 87HV.

[0043] Example 2

[0044] The activated iron matrix was kept in a ceramic fiber heat treatment furnace at 550℃ for 2 minutes and 50 seconds to 350℃; the preheated iron matrix was hot-dipped in an aluminum alloy melt at 770℃ for 3 minutes; the hot-dipped iron matrix was clamped into a mold at 200℃ and fixed, and an aluminum alloy melt at 700℃ was poured in 5 seconds to obtain an aluminum-iron composite material; a ceramic fiber furnace was selected as the heat treatment furnace, the aluminum-iron composite material was cooled to room temperature, and then heated to the target temperature at a heating rate of 3℃ / min in the heat treatment furnace, kept at 280℃ for 2.5h, and then slowly furnace-cooled to obtain a treated aluminum-iron composite material, which was subjected to shear strength testing and microhardness testing, and the shear strength was 21MPa and the average microhardness was 88HV.

[0045] Example 3

[0046] The activated iron matrix was kept in a ceramic fiber heat treatment furnace at 550℃ for 2 minutes and 50 seconds to 350℃; the preheated iron matrix was hot-dipped in an aluminum alloy melt at 790℃ for 3 minutes; the hot-dipped iron matrix was clamped into a mold at 200℃ and fixed, and an aluminum alloy melt at 720℃ was poured in 5 seconds to obtain an aluminum-iron composite material; a ceramic fiber furnace was selected as the heat treatment furnace, the aluminum-iron composite material was cooled to room temperature, and then heated to the target temperature at a heating rate of 5℃ / min in the heat treatment furnace, kept at 320℃ for 3.5h, and then slowly furnace-cooled to obtain a treated aluminum-iron composite material, which was subjected to shear strength testing and microhardness testing, and the shear strength was 17MPa and the average microhardness was 78HV.

[0047] Comparative Example 1

[0048] The activated iron substrate was kept in a ceramic fiber heat treatment furnace at 550°C for 2 minutes and 50 seconds to 350°C; the preheated iron substrate was hot-dipped in an aluminum alloy melt at 780°C for 3 minutes; the hot-dipped iron substrate was clamped into a mold at 200°C and fixed, and an aluminum alloy melt at 710°C was poured in 5 seconds to obtain an aluminum-iron composite material, which was subjected to shear strength test and microhardness test, and the shear strength was 11.5 MPa and the average microhardness was 100 HV.

[0049] Comparative Example 2

[0050] The activated iron substrate was kept in a ceramic fiber heat treatment furnace at 550°C for 2 minutes and 50 seconds to 350°C; the preheated iron substrate was hot-dipped in an aluminum alloy melt at 780°C for 3 minutes; the hot-dipped iron substrate was clamped into a mold at 200°C and fixed, and an aluminum alloy melt at 710°C was poured in 5 seconds to obtain an aluminum-iron composite material, which was subjected to shear strength test and microhardness test, and the shear strength was 11.5 MPa and the average microhardness was 100 HV.

[0051] Comparative Example 3

[0052] The activated iron substrate was kept in a ceramic fiber heat treatment furnace at 550°C for 2 minutes and 50 seconds to 350°C; the preheated iron substrate was hot-dipped in an aluminum alloy melt at 780°C for 3 minutes; the hot-dipped iron substrate was clamped into a mold at 200°C and fixed, and an aluminum alloy melt at 710°C was poured in 5 seconds to obtain an aluminum-iron composite material, which was subjected to shear strength test and microhardness test, and the shear strength was 11.5 MPa and the average microhardness was 100 HV.

[0053] Comparative Example 4

[0054] The activated iron substrate is kept in a ceramic fiber heat treatment furnace at 500°C for 2 minutes to 340°C; the preheated iron substrate is hot-dipped in an aluminum alloy melt at 780°C for 3 minutes; the hot-dipped iron substrate is clamped into a mold at 200°C and fixed, and an aluminum alloy melt at 700°C is poured in 5 seconds to obtain an aluminum-iron composite material; a ceramic fiber furnace is selected as the heat treatment furnace, the aluminum-iron composite material is cooled to room temperature, and then heated to the target temperature at a heating rate of 3°C / min in the heat treatment furnace, kept at 250°C for 3h, and then slowly furnace-cooled to obtain a treated aluminum-iron composite material, which is subjected to shear strength testing and microhardness testing, and the shear strength is 19 MPa and the microhardness is 89 HV.

[0055] Comparative Example 5

[0056] The activated iron substrate is kept in a ceramic fiber heat treatment furnace at 500°C for 2 minutes to 340°C; the preheated iron substrate is hot-dipped in an aluminum alloy melt at 780°C for 3 minutes; the hot-dipped iron substrate is clamped into a mold at 200°C and fixed, and an aluminum alloy melt at 700°C is poured in 5 seconds to obtain an aluminum-iron composite material; a ceramic fiber furnace is selected as the heat treatment furnace, the aluminum-iron composite material is cooled to room temperature, and then heated to the target temperature at a heating rate of 3°C / min in the heat treatment furnace, kept at 350°C for 3h, and then slowly furnace-cooled to obtain a treated aluminum-iron composite material, which is subjected to shear strength testing and microhardness testing, and the shear strength is 15 MPa and the microhardness is 76 HV.

[0057] Please refer to Figure 1 , Figure 1 are micrographs of the aluminum-iron composite materials after heat treatment in Example 1, Comparative Example 4 and Comparative Example 5, wherein, Figure 1 a in the micrograph is a micrograph of the aluminum-iron composite material after furnace cooling at 250°C for 3h in Comparative Example 4, Figure 1 b in the micrograph is a micrograph of the aluminum-iron composite material after furnace cooling at 300°C for 3h in Example 1, Figure 1 c in the micrograph is a micrograph of the aluminum-iron composite material after furnace cooling at 350°C for 3h in Comparative Example 5. After different temperature holding treatments and removal of excess aluminum alloy, Figure 1 a in the micrograph has relatively obvious cracks in the metallurgical reaction layer, Figure 1 b in the micrograph has no cracks in the metallurgical reaction layer, Figure 1 c in the micrograph also has relatively narrow cracks in the metallurgical reaction layer.

[0058] Please refer to Figure 2 , Figure 2The image shows the XRD stress diagram of the aluminum-iron composite material after heat treatment in Example 1 of this application. The residual stress value of the aluminum-iron composite material after heat treatment is obtained by XRD residual stress test on the aluminum side near the metallurgical reaction layer. The residual stress value on the aluminum side is 15.2±1.6MPa, which ensures the quality of the aluminum / iron bimetallic interface.

[0059] Please see Figure 3 , Figure 4 as well as Figure 5 , Figure 3 This is a microscopic image of the aluminum-iron composite material in Comparative Example 1 of this application. Figure 4 This is the XRD stress diagram of the aluminum-iron composite material in Comparative Example 1 of this application. Figure 5 The images shown are physical and microscopic views of the aluminum-iron composite material in Comparative Example 1 of this application after being cut. Figure 3 The aluminum-iron composite material shown has a metallurgical reaction layer at the composite interface, which is relatively straight and has a thickness of about 5 μm. At this point, the interface does not crack. Figure 4 The aluminum side of the aluminum-iron composite material has a residual stress of 73.9 ± 10.1 MPa. Figure 5 In Comparative Example 1, the aluminum-iron composite material was not heat-treated. Excess aluminum alloy bearing the interfacial stress of the aluminum-iron was removed by wire cutting. Figure 5 The image shows a macroscopic view of the wire-cut area and a metallographic image of the aluminum-iron interface after stress release. It can be seen that the residual stress at the aluminum / iron bimetallic interface pulls the metallurgical reaction layer apart, forming a crack of about 5 μm.

[0060] Please see Figure 6 and Figure 7 , Figure 6 Microscopic images of the aluminum-iron composite materials in Comparative Examples 2 and 3 of this application; Figure 7 a, Figure 7 b, Figure 7 In the diagrams c, microscopic images of the untreated aluminum-iron composite materials from Comparative Examples 1, 2, and 3 of this application are shown. Figure 6 Image a shows a microscopic image of an aluminum-iron composite material obtained by hot-dip molten aluminum alloy into an iron matrix at 700℃. Figure 6 Image b shows a microscopic image of an aluminum-iron composite material obtained by hot-dip molten aluminum alloy into an iron matrix at 750℃. Even with appropriate temperature holding after heat treatment, heat treatment at 300℃ for 3 hours is insufficient to induce significant elemental diffusion. At 700℃, no metallurgical reaction layer is formed, and large cracks remain. While some metallurgical reaction layer is formed during hot-dip immersion at 730℃, areas without this layer still exist. These areas, lacking a metallurgical reaction layer, are mechanically joined, resulting in insufficient bonding strength and performance. Figure 6 a and Figure 6 The sample represented by 'b' in the diagram undergoes a shear strength test.Figure 6 The sample represented by a has no bonding, and the aluminum and iron have been separated during processing into a shear sample, Figure 6 The shear strength of the sample represented by b is only less than 6.7 MPa.

[0061] In the above examples, through the comparison of Example 1 and Comparative Example 1, the heat treatment method provided by the present application, i.e., heat treatment at 300 DEG C for 3 hours and then slow furnace cooling, although does not change the element composition of the metallurgical reaction layer, on the one hand reduces the residual stress on the aluminum side, and on the other hand, this annealing heat treatment can eliminate the composition segregation and dissolved non-equilibrium phase of the aluminum alloy, and these common factors can reduce the "pressure" of the aluminum side on the metallurgical reaction layer, thereby ensuring the bonding and shear strength of the aluminum / iron bimetallic metallurgical interface. The inventors found through Example and Comparative Examples 2 and 3 that selecting a temperature of 780 DEG C + / - 10 DEG C for hot dipping can achieve the technical effects in the heat treatment scheme of the present application; the inventors found through Example and Comparative Examples 4 and 5 that the heat treatment temperature and time of 280-320 DEG C for 2.5-3.5 hours can achieve the technical effects of the present application.

[0062] The present application controls the temperature during hot dipping of the iron base material, and performs heat treatment on the cast aluminum-iron composite material at a certain temperature and time, thereby achieving the effect of reducing the interfacial stress of the aluminum-iron composite material, on the one hand weakening the stress on the aluminum side in the liquid-solid composite aluminum / iron bimetal, and on the other hand ensuring the integrity of the aluminum / iron bimetal interface metallurgical bonding and improving the shear strength of the aluminum / iron bimetal; on the other hand, after the release of the residual stress of the aluminum / iron bimetal, the as-cast aluminum / iron bimetal sample can be processed more freely and more selectively, and the aluminum / iron bimetal interface is ensured to be complete after processing.

[0063] The above only describes the preferred embodiments of the present application, and does not limit the patent scope of the present application, and any equivalent structural transformation made according to the content of the present application, or direct / indirect application in other related technical fields is included in the patent protection scope of the present application.

Claims

1. A method of treating the interface stress of an aluminum-iron composite material, characterized by, The method comprises the following steps: S1, activating the surface of the iron base material; S2, hot-dipping the iron base material with a first aluminum material, and casting the hot-dipped iron base material with a second aluminum material to obtain the aluminum-iron composite material, wherein the first aluminum material is molten aluminum at 785-790 DEG C, and the second aluminum material is molten aluminum at 700-720 DEG C; S3, heating the aluminum-iron composite material to 320 DEG C at a heating rate of 3-5 DEG C / min, and holding for 3.5 h, and then furnace cooling the aluminum-iron composite material; Before the step S2, the iron base material is preheated at a temperature of 500-600 DEG C for 2-3 min to heat the iron base material to 355-360 DEG C; In the step S2, the residual stress on the aluminum side of the aluminum-iron composite material is 60-90 MPa; In the step S3, the residual stress on the aluminum side of the aluminum-iron composite material is 12-18 MPa; The aluminum-iron composite material comprises an aluminum coating layer, the aluminum coating layer comprises a metallurgical reaction layer and a hot-dip melt layer, the metallurgical reaction layer comprises Al5Fe2, Al 13 Fe4, the thickness of the metallurgical reaction layer is 4-6 μm, and the thickness of the aluminum coating layer is 10-14 μm.

2. The method of claim 1, wherein the aluminum-iron composite interface stress treatment method is characterized by, In the step S1, the activation treatment comprises grinding, alkali washing, and acid washing.

3. The method of claim 1, wherein the aluminum-iron composite material is an aluminum-iron clad material. In the step S1, the iron base material is iron or steel; and in the step S2, the first aluminum material and the second aluminum material are aluminum or aluminum alloy.

4. An aluminum-iron composite material, characterized by, The aluminum-iron composite material is prepared by the aluminum-iron composite material interface stress treatment method according to any one of claims 1-3.

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