Reinforced aluminum alloy composite material, method for manufacturing the same, and application thereof, and aluminum alloy drill pipe body and method for manufacturing the same

Abstract

This invention relates to the field of oil pipe and equipment materials, and discloses a reinforced aluminum alloy composite material, its preparation method and application, and a method for preparing an aluminum alloy drill pipe body. The composite material comprises an aluminum alloy matrix phase and an egg-shaped cerium-ceramic reinforcing phase dispersed in the matrix phase. The content of the reinforcing phase, based on the total weight of the composite material, is 0.2-0.5 wt%. The egg-shaped cerium-ceramic reinforcing phase includes a ceramic oxide core layer, a cerium-aluminum alloy intermediate layer, and a cerium-aluminum alloy metal oxide film layer in the intermediate layer. This reinforced aluminum alloy composite material exhibits high strength at both room temperature and high temperature, and good extrusion molding performance, making it particularly suitable for the preparation of large / long (10m long) oil pipes.

Description

Technical Field

[0001] This invention relates to the field of oil pipe and equipment materials, specifically to a reinforced aluminum alloy composite material, its preparation method and application, and an aluminum alloy drill pipe body and its preparation method. Background Technology

[0002] With the exploration and development of deep and ultra-deep oil and gas, conventional steel drill pipes are prone to damage and failure due to their high density and insufficient corrosion resistance, seriously affecting drilling efficiency and safety. Aluminum alloy drill pipe materials, characterized by high strength, low density, fatigue resistance, and corrosion resistance, represent a superior technology for solving drill string failure in ultra-deep wells. Existing patents cover aluminum alloy drill pipe materials with pressures of 325MPa (CN 201310114425.0), 480MPa (CN 201510142849.7), 580MPa (CN201410855573.2), and 620MPa (CN 201410853240.6), which can serve for extended periods in downhole conditions with operating temperatures not exceeding 120℃ or 160℃, thus addressing drilling problems in wells shallower than 6000 meters to a certain extent. However, the maximum drilling depth of ultra-deep wells in my country has reached tens of thousands of meters, with bottom hole temperatures exceeding 180°C. Existing aluminum alloy drill pipe materials can no longer meet the requirements of ultra-deep oil and gas drilling. Therefore, there is an urgent need to develop high-temperature resistant aluminum alloy drill pipe materials to meet the high-temperature drilling requirements of ultra-deep oil and gas formations. Summary of the Invention

[0003] The purpose of this invention is to provide a reinforced aluminum alloy composite material, its preparation method and application, and an aluminum alloy drill pipe body and its preparation method. The reinforced aluminum alloy composite material has high strength at room temperature and high temperature, good extrusion molding performance, and is particularly suitable for the preparation of large / long (10m long) oil pipes.

[0004] According to a first aspect of the present invention, the present invention provides a reinforced aluminum alloy composite material comprising an aluminum alloy matrix phase and an egg-shaped metal-ceramic particle reinforcing phase dispersed in the matrix phase, wherein the content of the reinforcing phase is 0.2-0.5 wt% based on the total weight of the composite material; the egg-shaped metal-ceramic particle reinforcing phase comprises a ceramic oxide core layer, a cerium-aluminum alloy intermediate layer, and an oxide film layer formed by the cerium-aluminum alloy metal of the intermediate layer.

[0005] According to a second aspect of the present invention, the present invention provides a method for preparing the reinforced aluminum alloy composite material of the present invention, the method comprising: (1) depositing a cerium-aluminum alloy intermediate layer on the surface of ceramic oxide powder, reacting it with oxygen to generate an oxide film layer, cooling it to obtain egg-shaped metal ceramic particles as the reinforcing phase, the egg-shaped metal ceramic particles comprising a ceramic oxide core layer, a cerium-aluminum alloy intermediate layer and an oxide film layer formed by the cerium-aluminum alloy metal of the intermediate layer; preparing an aluminum alloy melt as the matrix phase; (2) adding the metal ceramic particles obtained in step (1) to the aluminum alloy melt, melting and cooling it to form an ingot.

[0006] According to a third aspect of the present invention, the present invention provides an application of the reinforced aluminum alloy composite material described herein in the preparation of oil pipes.

[0007] According to a fourth aspect of the present invention, the present invention provides an aluminum alloy drill pipe body, wherein the material of the aluminum alloy drill pipe body is the composite material described in the present invention.

[0008] According to a fifth aspect of the present invention, the present invention provides a method for preparing an aluminum alloy drill pipe body, the method comprising: melting, casting, extruding, solution treatment, and aging treatment of the composite material described in the present invention to obtain an aluminum alloy drill pipe body.

[0009] In the reinforced aluminum alloy composite material of this invention, the egg-shaped cerium-ceramic reinforcement phase has a dispersion strengthening effect on the aluminum alloy matrix phase, which can effectively improve the strength of the aluminum alloy composite material. The cerium-ceramic reinforcement phase has an "egg" structure of "ceramic oxide core layer / cerium-aluminum alloy intermediate layer / oxide thin film layer", which has higher toughness compared with the pure ceramic phase. In subsequent applications, such as tube extrusion molding, the two-dimensional oxide thin film layer can deform without breaking within a certain deformation range as the metal toughening intermediate layer deforms. The presence of this special reinforcement phase improves the material strength without affecting the subsequent tube extrusion molding performance. Detailed Implementation

[0010] The endpoints and any values ​​of the ranges disclosed herein are not limited to the precise ranges or values, and these ranges or values ​​should be understood to include values ​​close to these ranges or values. For numerical ranges, the endpoint values ​​of the various ranges, the endpoint values ​​of the various ranges and individual point values, and individual point values ​​can be combined with each other to obtain one or more new numerical ranges, which should be considered as specifically disclosed herein.

[0011] This invention provides a reinforced aluminum alloy composite material. The composite material comprises an aluminum alloy matrix phase and an egg-shaped metal-ceramic particle reinforcing phase dispersed within the matrix phase. The content of the reinforcing phase, based on the total weight of the composite material, is 0.2-0.5 wt%. The egg-shaped metal-ceramic particle reinforcing phase comprises a ceramic oxide core layer, a cerium-aluminum alloy intermediate layer, and an oxide film layer formed by the cerium-aluminum alloy metal of the intermediate layer. The egg-shaped metal-ceramic particle reinforcing phase of this invention has an "egg" structure of "ceramic oxide core layer / cerium-aluminum alloy intermediate layer / oxide film layer," where the ceramic oxide core layer resembles the yolk of an egg, the cerium-aluminum alloy intermediate layer resembles the egg white, and the oxide film layer resembles the eggshell.

[0012] According to a preferred embodiment of the present invention, the diameter of the egg-shaped metal-ceramic particles of the present invention is 100-145 nm.

[0013] In this invention, there is no special limitation on the specific type of ceramic oxide in the egg-shaped metal-ceramic reinforcing phase. In the embodiments of this invention, cerium oxide is used as an example to illustrate the advantages of this invention, but this does not limit the scope of this invention.

[0014] According to a preferred embodiment of the present invention, the ceramic oxide in the egg-shaped metal-ceramic particles has a particle size of 5-20 nm. Nanoscale ceramic oxides have a grain boundary fixing effect and dispersion strengthening effect, and the composite material of the present invention, satisfying the aforementioned characteristics, exhibits higher strength and better extrusion molding performance under high-temperature conditions.

[0015] In this invention, the specific type and aluminum content of the cerium-aluminum alloy in the egg-shaped metal ceramic particles are not specifically limited. The following is an illustrative description, but it does not limit the scope of the invention. According to a preferred embodiment of the invention, the cerium-aluminum alloy is a Ce-Al master alloy, in which the Al content is 75-85 wt% and the remainder is Ce.

[0016] According to a preferred embodiment of the present invention, in the egg-shaped metal ceramic particles, the oxide film layer comprises CeO2 and α-Al2O3, and the content of alumina accounts for 60-85 wt% of the oxide.

[0017] In this invention, the oxide film comprises CeO2 and α-Al2O3. The inventors discovered that, since the oxide film corresponding to the Ce-Al master alloy is CeO2 and α-Al2O3, and because the composite material lacks O atoms, the CeO2 and α-Al2O3 in the oxide film will not grow. Furthermore, CeO2 and α-Al2O3 are extremely stable at high temperatures, such as 800°C, and will not decompose, effectively improving performance. Therefore, the reinforcing phase satisfying the aforementioned characteristics is more stable at high temperatures, and the aluminum alloy drill pipe material prepared using the composite material exhibits higher structural stability and high-temperature strength at high temperatures.

[0018] In this invention, there are no special requirements for the thickness of the cerium-aluminum alloy interlayer in the egg-shaped cerium-ceramic particles. The following is an illustrative description, but it does not limit the scope of the invention. According to a preferred embodiment of the invention, the thickness of the cerium-aluminum alloy interlayer is 40-50 nm. The cerium-ceramic reinforcing phase that meets the aforementioned characteristics has a good dispersion effect in the aluminum alloy matrix phase.

[0019] According to a preferred embodiment of the present invention, in the egg-shaped cerium-aluminum alloy intermediate layer to the oxide film layer in the cerium-aluminum alloy cerium-ceramic particles, the thickness ratio is 4-5:1. The cerium-ceramic particles satisfying the aforementioned characteristics exhibit good dispersion in the aluminum alloy matrix phase.

[0020] In this invention, there are no special requirements regarding the types and contents of metals contained in the aluminum alloy matrix phase. The following is an illustrative description, but it does not limit the scope of the invention. According to a preferred embodiment of the invention, the aluminum alloy matrix phase contains 4-4.8 wt% Cu, 1.5-2.0 wt% Mg, 0.7-0.9 wt% Mn, 0.5-0.9 wt% Ni, 0.3-0.5 wt% Zn, 0.005-0.008 wt% B, with the balance being Al and unavoidable impurities. The composite material of the present invention, satisfying the foregoing characteristics, has better room temperature and high temperature strength.

[0021] In this invention, there is no special limitation on the preparation method of the composite material described in this invention. The following is an illustrative description, but it does not limit the scope of this invention. This invention provides a preparation method of the reinforced aluminum alloy composite material described in this invention. The method includes: (1) depositing a cerium aluminum alloy intermediate layer on the surface of ceramic oxide powder, reacting it with oxygen to generate an oxide film layer, cooling it, and obtaining egg-shaped metal ceramic particles as the reinforcing phase. The egg-shaped metal ceramic particles include a ceramic oxide core layer, a cerium aluminum alloy intermediate layer, and an oxide film layer formed by the cerium aluminum alloy metal of the intermediate layer; preparing an aluminum alloy melt as the matrix phase; (2) adding the metal ceramic particles obtained in step (1) to the aluminum alloy melt, melting and cooling it to form an ingot.

[0022] In this invention, there is no particular limitation on the deposition method described in step (1). According to a preferred embodiment of the present invention, magnetron sputtering is used as an exemplary deposition method to illustrate the advantages of the technical solution of this application, but this does not limit the scope of the present invention. Magnetron sputtering can more precisely control the thickness of the cerium-aluminum alloy intermediate layer and the oxide film layer of the reinforcing phase. Before magnetron sputtering deposition, in order to remove contaminants and adsorbates on the surface of the ceramic oxide powder, the ceramic oxide powder was ultrasonically cleaned with acetone, ethanol and deionized water for 10 minutes in sequence, dried and spread flat on the substrate stage.

[0023] In this invention, there are no special requirements for the sputtering power of the magnetron sputtering. The following is an illustrative description, but it does not limit the scope of the invention. According to a preferred embodiment of the invention, the sputtering power is 310-320W.

[0024] In this invention, there are no special requirements for the sputtering gas pressure of the magnetron sputtering, for example, it is 0.5-0.8 Pa.

[0025] In this invention, there are no special requirements for the substrate temperature of the magnetron sputtering. The following is an illustrative description, but it does not limit the scope of the invention. According to a preferred embodiment of the invention, the substrate temperature is 250-260°C.

[0026] In this invention, there are no special requirements for the deposition time in step (1), but the thickness of the intermediate layer should not exceed 50 nm. The following is an illustrative description, but it does not limit the scope of the invention. According to a preferred embodiment of the invention, the deposition time is 120-150 s.

[0027] In this invention, in step (1), the deposition can be carried out in an inert atmosphere. There are no special requirements for the specific type of deposition atmosphere. The following is an illustrative description, but it does not limit the scope of this invention. According to a preferred embodiment of this invention, the deposition atmosphere is an argon atmosphere.

[0028] In this invention, there are no special requirements for the flow rate of the argon atmosphere. The following is an illustrative description, but it does not limit the scope of the invention. According to a preferred embodiment of the invention, the flow rate of the argon atmosphere is 20-25 mL / min.

[0029] In this invention, in step (1), after depositing a cerium-aluminum alloy intermediate layer on the surface of ceramic oxide powder, it is reacted with oxygen to generate an oxide film layer. There are no special requirements for the temperature of the contact reaction. The following is an illustrative description, but it does not limit the scope of the invention. According to a preferred embodiment of the invention, the temperature of the contact reaction is 250-260°C.

[0030] In this invention, there are no special requirements for the contact reaction time in step (1). The following is an illustrative description, but it does not limit the scope of the invention. According to a preferred embodiment of the invention, the contact reaction time is 40-50 seconds.

[0031] In this invention, in step (1), argon gas is introduced during the deposition of the cerium-aluminum alloy intermediate layer, and argon gas and oxygen gas are introduced simultaneously during the contact reaction stage.

[0032] According to a preferred embodiment of the present invention, in step (1), the contact reaction is carried out in an argon atmosphere. By employing the aforementioned technical solution, the contact reaction becomes more stable, and the resulting oxide film becomes denser.

[0033] In this invention, during step (1) of the contact reaction process, there are no special requirements for the flow rate of the oxygen gas. The following is an illustrative description, but it does not limit the scope of the invention. According to a preferred embodiment of the invention, the flow rate of the oxygen is 0.4-0.5 mL / min. In this invention, the introduction of extremely low oxygen content is beneficial to the formation of α-Al2O3 and CeO2 structures in the film layer, thereby improving the high-temperature strength of the aluminum alloy drill rod material. Due to the extremely low oxygen content, due to the selective oxidation characteristics (at 260°C, the Gibbs free energy of α-alumina formation is below -1000 kJ / mol, and that of cerium oxide is above -700 kJ / mol), α-Al2O3 will be preferentially generated on the surface of the cerium-aluminum alloy. For example, when the aluminum alloy is a Ce / Al intermediate alloy, a nano-oxide film mainly composed of α-Al2O3 and containing a small amount of CeO2 will be generated on the alloy surface. Because the diffusion coefficient of elements in heterogeneous oxides is extremely low, CeO2 and α-Al2O3 mutually restrict the transformation of their nanoparticles into macroscopic crystals. This unique structure significantly reduces the impact of size effects on the thermodynamic properties of nano-oxide particles. Specifically, it limits the growth of the CeO2 and α-Al2O3 nanoparticles used for reinforcement, which is beneficial for improving the high-temperature strength of aluminum alloy drill pipe materials.

[0034] In this invention, during step (1) of the contact reaction process, there are no special requirements for the flow rate of the argon atmosphere. The following is an illustrative description, but it does not limit the scope of the invention. According to a preferred embodiment of the invention, the flow rate of the argon is 20-25 mL / min.

[0035] In this invention, in step (1), before deposition, the reaction environment needs to be evacuated to 0.001-0.003 Pa, and the sample surface needs to be bombarded with argon gas for 2-5 minutes to remove sample contaminants.

[0036] In this invention, after the contact reaction is completed, the metal-ceramic powder is removed after cooling to room temperature. This is a routine operation and will not be described in detail here.

[0037] In this invention, in step (2), the melting process enables the metal ceramic powder to be fully dispersed in the aluminum alloy matrix melt. The melting temperature is preferably such that the cerium aluminum alloy is fully melted and the low-melting-point metals such as magnesium are oxidized and burned off. The following is an illustrative description, but it does not limit the scope of this invention. According to a preferred embodiment of this invention, the melting temperature is 700-720°C.

[0038] In this invention, the melting time in step (2) can be selected from a wide range. The following is an illustrative description, but it does not limit the scope of this invention. According to a preferred embodiment of this invention, the melting time is 10-15 min.

[0039] The reinforced aluminum alloy composite material of the present invention has high strength and good extrusion molding performance, and is particularly suitable for use in the preparation of large / long oil pipes.

[0040] This invention provides an aluminum alloy drill pipe body, the material of which is the composite material described in this invention. This aluminum alloy drill pipe body exhibits excellent structural stability and high-temperature strength at high temperatures.

[0041] This invention provides a method for preparing an aluminum alloy drill pipe body, the method comprising: melting, casting, homogenizing the cast billet, multi-stage extrusion molding, multi-stage solution treatment, and aging treatment of the composite material described in this invention to obtain the aluminum alloy drill pipe body.

[0042] In this invention, the smelting, casting, billet homogenization, and extrusion molding are all conventional operations well known to those skilled in the art, and will not be described in detail here. No special requirements are made for their specific conditions.

[0043] In this invention, as long as the temperature of the secondary solution is higher than that of the primary solution and the time of the secondary solution is longer than that of the primary solution, no special requirements are made for the specific conditions of the primary solution. The following is an illustrative description, but it does not limit the scope of the invention. According to a preferred embodiment of the invention, the conditions of the primary solution include: a temperature of 480-495°C; and / or a time of 40-60 min.

[0044] In this invention, as long as the temperature of the secondary solution is higher than that of the primary solution and the time of the secondary solution is longer than that of the primary solution, no special requirements are made for the specific conditions of the secondary solution. The following is an illustrative description, but it does not limit the scope of the invention. According to a preferred embodiment of the invention, the conditions of the secondary solution include: a temperature of 495-510°C; and / or a time of 70-80 min.

[0045] In this invention, there are no special requirements for the aging process. The following is an illustrative description, but it does not limit the scope of the invention. According to a preferred embodiment of the invention, the aging process includes a first-stage high-temperature aging and a second-stage air-cooled aging.

[0046] In this invention, there are no special requirements for the conditions of the first-stage high-temperature aging. The following is an illustrative description, but it does not limit the scope of the invention. According to a preferred embodiment of the invention, the conditions of the first-stage high-temperature aging are: temperature of 190-200℃; and / or time of 1.5-2h.

[0047] In this invention, there are no special requirements for the conditions of the secondary air-cooled aging process. The following is an illustrative description, but it does not limit the scope of the invention. According to a preferred embodiment of the invention, the conditions of the secondary air-cooled aging process include: a temperature of 15-25°C; and / or a time of 10-12 days.

[0048] The aluminum alloy drill pipe body prepared by this invention has a yield strength of not less than 380 MPa and a heat resistance temperature of up to 180℃. After being exposed to heat at 180℃ for 500 hours, its yield strength can still maintain 72% of the room temperature value. It can be applied to drilling of deep and ultra-deep oil and gas formations, providing material support for lightweight technology in deep and ultra-deep well drilling.

[0049] The present invention will be described in detail below through embodiments.

[0050] In the following embodiments, The magnetron sputtering equipment is a desktop magnetron sputtering equipment, model MS-400, manufactured by Hefei Zhizhen Precision Equipment Co., Ltd. The particle size of cerium oxide powder, the diameter of egg-shaped cerium-ceramic particles, the thickness of the cerium-aluminum alloy interlayer, and the thickness of the oxide film were obtained by measuring the embedded particle samples using transmission electron microscopy and taking the average value. The composition of the material can be obtained through material input calculations; The room temperature and high temperature yield strengths of the aluminum alloy drill pipe were measured using a mechanical testing machine. The argon gas is high-purity argon gas (99.99%), and the oxygen gas is high-purity O2 (99.99%).

[0051]

Preparation Example 1

[0052] (2) The cermet powder prepared in step (1) is added to an aluminum alloy-based solution (the components by weight are: Cu 4%, Mg 1.5%, Mn 0.7%, Ni 0.5%, Zn 0.3%, B 0.005%, with the balance being Al and unavoidable impurities). The amount of cermet powder added is 0.2% by weight of the total material. The mixture is melted (at a temperature of 700°C for 10 min), cooled to room temperature, and an ingot is formed to obtain the composite material.

[0053]

Preparation Example 2

[0054] (2) The cermet powder prepared in step (1) is added to the aluminum alloy-based solution (the components by weight are: Cu 4.5%, Mg 1.7%, Mn 0.8%, Ni 0.6%, Zn 0.4%, B 0.006%, with the balance being Al and unavoidable impurities), wherein the amount of cermet powder added is 0.3% by weight of the total material. The mixture is melted (at a temperature of 700℃ for 10 min), cooled to room temperature, and an ingot is formed to obtain the composite material.

[0055]

Preparation Example 3

[0056]

Preparation Example 4

[0057]

Preparation Example 5

[0058]

Preparation Example 6

[0059]

Preparation Example 7

[0060] (2) The cermet powder prepared in step (1) is added to the aluminum alloy-based solution (the components by weight are: Cu 4%, Mg 1.5%, Mn 0.7%, Ni 0.5%, Zn 0.3%, B 0.005%, with the balance being Al and unavoidable impurities). The amount of cermet powder added is 0.2% by weight of the total material. The mixture is melted (at a temperature of 700℃ for 10 min), cooled to room temperature, and an ingot is formed to obtain the composite material.

[0061]

Preparation Example 8

[0062] (2) The cermet powder prepared in step (1) is added to the aluminum alloy-based solution (the components by weight are: Cu 4%, Mg 1.5%, Mn 0.7%, Ni 0.5%, Zn 0.3%, B 0.005%, with the balance being Al and unavoidable impurities). The amount of cermet powder added is 0.2% by weight of the total material. The mixture is melted (at a temperature of 700℃ for 10 min), cooled to room temperature, and an ingot is formed to obtain the composite material.

[0063]

Preparation Example 9

[0064]

Example 1

[0065]

Example 2

[0066]

Example 3

[0067]

Example 4

[0068]

Example 5

[0069]

Example 6

[0070]

Example 7

[0071] Comparative Example 1 The method of Example 1 is followed, except that the composite material obtained in Preparation Example 8 is used to process the aluminum alloy drill pipe body.

[0072] Comparative Example 2 The method of Example 1 is followed, except that the composite material obtained in Preparation Example 9 is used to process the aluminum alloy drill pipe body.

[0073] The yield strength of the aluminum alloy drill pipe materials prepared in the above embodiments and comparative examples was tested, and the specific data are shown in Table 1.

[0074] Table 1

[0075] The preferred embodiments of the present invention have been described in detail above; however, the present invention is not limited thereto. Within the scope of the inventive concept, various simple modifications can be made to the technical solutions of the present invention, including combinations of various technical features in any other suitable manner. These simple modifications and combinations should also be considered as the content disclosed in the present invention and are all within the protection scope of the present invention.

Claims

1. A reinforced aluminum alloy composite material, characterized in that, The composite material comprises an aluminum alloy matrix phase and an egg-shaped metal-ceramic particle reinforcing phase dispersed in the matrix phase, wherein the content of the reinforcing phase is 0.2-0.5 wt% based on the total weight of the composite material. The egg-shaped metal-ceramic particle reinforcement phase includes a ceramic oxide core layer, a cerium-aluminum alloy intermediate layer, and an oxide film layer formed by the cerium-aluminum alloy metal of the intermediate layer.

2. The composite material according to claim 1, characterized in that, The diameter of the egg-shaped metal-ceramic particles is 100-145 nm; and / or In the egg-shaped metal-ceramic particles The ceramic oxide is cerium oxide; and / or The thickness of the ceramic oxide core layer is 5-20 nm.

3. The composite material according to claim 1 or 2, characterized in that, In the egg-shaped metal-ceramic particles The cerium-aluminum alloy is a Ce-Al master alloy, with an Al content of 75-85 wt%; and / or The oxide film consists of CeO2 and α-Al2O3, with the content of α-Al2O3 being 60-85 wt%.

4. The composite material according to claim 1 or 2, characterized in that, In the egg-shaped metal-ceramic particles The thickness of the cerium-aluminum alloy interlayer is 40-50 nm; and / or The thickness ratio of the cerium-aluminum alloy intermediate layer to the oxide film layer is 4-5:

1.

5. The composite material according to claim 1 or 2, characterized in that, The aluminum alloy matrix contains 4-4.8 wt% Cu, 1.5-2.0 wt% Mg, 0.7-0.9 wt% Mn, 0.5-0.9 wt% Ni, 0.3-0.5 wt% Zn, 0.005-0.008 wt% B, with the balance being Al and unavoidable impurities.

6. A method for preparing the reinforced aluminum alloy composite material according to claim 1 or 2, characterized in that, The method includes: (1) After depositing a cerium-aluminum alloy intermediate layer on the surface of ceramic oxide powder, it reacts with oxygen to generate an oxide film layer. After cooling, egg-shaped metal ceramic particles as the reinforcing phase are obtained. The egg-shaped metal ceramic particles include a ceramic oxide core layer, a cerium-aluminum alloy intermediate layer and an oxide film layer formed by the cerium-aluminum alloy metal of the intermediate layer; an aluminum alloy melt as the matrix phase is prepared. (2) The metal ceramic particles obtained in step (1) are added to the aluminum alloy melt, smelted and cooled to form an ingot.

7. The method according to claim 6, characterized in that, In step (1), the deposition is performed using magnetron sputtering.

8. The method according to claim 7, characterized in that, The conditions for magnetron sputtering include: The sputtering power is 310-320W; and / or The substrate temperature is 250-260℃.

9. The method according to claim 6 or 7, characterized in that, In step (1), the deposition conditions include: The time is 120-150 seconds; and / or The deposition atmosphere was argon.

10. The method according to claim 9, characterized in that, In step (1), the flow rate of the argon atmosphere is 20-25 mL / min.

11. The method according to claim 6 or 7, characterized in that, In step (1), the conditions for the contact reaction include: The temperature is 250-260℃; and / or The time is 40-50 seconds; and / or The reaction is carried out in an argon atmosphere.

12. The method according to claim 11, characterized in that, In step (1), The oxygen flow rate is 0.4-0.5 mL / min; and / or The flow rate of the argon gas is 20-25 mL / min.

13. The method according to claim 6 or 7, characterized in that, In step (2), the smelting conditions include: The melting temperature is 700-720℃; and / or The heat preservation time is 10-15 minutes.

14. The application of the reinforced aluminum alloy composite material according to claim 1 or 2 in the preparation of oil pipes.

15. An aluminum alloy drill pipe body, characterized in that, The material of the aluminum alloy drill pipe body is the composite material described in claim 1 or 2.

16. A method for preparing an aluminum alloy drill pipe body, characterized in that, The method includes: melting, casting, homogenizing the cast billet, multi-stage extrusion molding, multi-stage solution treatment, and aging treatment of the composite material described in claim 1 or 2 to obtain an aluminum alloy drill pipe body.

17. The method according to claim 16, characterized in that, The multi-stage solid solution includes primary solid solution and secondary solid solution. The temperature of the secondary solid solution is higher than that of the primary solid solution, and the time of the secondary solid solution is longer than that of the primary solid solution.

18. The method according to claim 17, characterized in that, The conditions for the primary solution treatment include: Temperature is 480-495℃; and / or The time is 40-60 minutes; and / or The conditions for the secondary solid solution include: Temperature is 495-510℃; and / or The time is 70-80 minutes.

19. The method according to claim 16, characterized in that, The aging process includes primary high-temperature aging and secondary air-cooled aging. The conditions for the first-level high-temperature aging include: Temperature is 190-200℃; and / or The time is 1.5-2 hours; and / or The conditions for the secondary air-cooling aging process include: The temperature is 15-25℃; and / or The time is 10-12 days.

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