A manufacturing method of bimetallic metallurgical composite pipeline pipe and bimetallic metallurgical composite pipeline pipe

Abstract

The present invention discloses a method for manufacturing a bimetallic metallurgical composite line pipe, which comprises the steps of: using a sulfur-resistant line pipe as a base pipe, and laser-cladding a functional alloy spherical powder on the inner wall of the base pipe to form a cladding layer, wherein the surface roughness of the cladding layer is 10-50 μm. Accordingly, the present invention also discloses a bimetallic metallurgical composite line pipe, which can be manufactured using the above-mentioned manufacturing method. The manufacturing cost of the manufacturing method is low, and a bimetallic metallurgical composite line pipe can be manufactured using the above-mentioned manufacturing method. The bimetallic metallurgical composite line pipe of the present invention can be used for oil and gas transportation in corrosive media containing H2S and CO2, which is of great significance to the oil and gas industry and has a very broad market prospect.

Description

Technical Field

[0001] The present invention relates to a steel pipe and a manufacturing method thereof, and in particular to a line pipe and a manufacturing method thereof. Background Art

[0002] In recent years, with the continued high demand for oil and gas resources and the gradual depletion of high-quality oil and gas fields, oil and gas exploration and production have continued to develop towards deep wells, ultra-deep wells and corrosive oil and gas wells.

[0003] During oil and gas gathering and transportation, environments rich in corrosive media such as H2S, CO2, and Cl- can cause corrosion damage to oil and gas gathering and transportation pipelines. To avoid failures under these harsh service conditions, line pipes must possess excellent comprehensive service performance.

[0004] Bimetallic composite pipes are becoming a major research area for pipes in the oil and gas industry, as they leverage the mechanical properties of the base pipe and the high corrosion resistance of the cladding layer while significantly reducing costs. They also fully comply with the requirements of the steel industry's "carbon neutrality" policy.

[0005] To date, researchers have conducted relevant research on bimetallic metallurgical composite pipes, but the metallurgical composite processes in the existing technology are mostly traditional metallurgical composite methods such as hot extrusion, hot rolling, explosive welding, surfacing composite or centrifugal casting, and the products are not pipeline pipes for oil and gas transportation.

[0006] Unlike the aforementioned prior art, the present invention aims to provide a novel method for manufacturing bimetallic metallurgical composite line pipe, which is simple to implement and has low production costs. This manufacturing method utilizes a laser to clad the inner wall of a base pipe with spherical functional alloy powder to form a cladding layer. This manufacturing method can effectively produce bimetallic metallurgical composite line pipe, which can be used in the oil and gas industry and has a very broad market prospect. Summary of the Invention

[0007] One of the objectives of the present invention is to provide a method for manufacturing bimetallic metallurgical composite line pipe. This method is simple to implement and has low production costs. This method can effectively produce bimetallic metallurgical composite line pipe that meets the requirements for high H2S and CO2 corrosion resistance and exhibits comparable mechanical properties. This method can be effectively applied in the oil and gas industry and has a very broad market prospect.

[0008] In order to achieve the above object, the present invention proposes a method for manufacturing a bimetallic metallurgical composite pipeline pipe, which comprises the following steps:

[0009] The sulfur-resistant line pipe is used as a base pipe, and functional alloy spherical powder is laser clad on the inner wall of the base pipe to form a cladding layer, wherein the surface roughness of the cladding layer is 10-50 μm.

[0010] In the above-mentioned technical solution of the present invention, the functional alloy is first formed into a spherical powder. This spherical powder is then laser-clad onto the inner wall of a base pipe to form a cladding layer, thereby enhancing the bimetallic metallurgical composite linepipe's resistance to H2S and CO2 corrosion. Ultra-high-speed laser cladding can be used for this process, which causes virtually no damage to the base pipe. The clad bimetallic metallurgical composite linepipe requires no further heat treatment and can be delivered directly as a finished product.

[0011] It should be noted that in actual operation, in order to meet specific H2S and CO2 corrosion performance requirements, operators can select different functional alloys according to needs, and base pipes can be selected from sulfur-resistant pipelines of different steel grades as needed.

[0012] Furthermore, in the manufacturing method of the present invention, the particle size of the functional alloy spherical powder is 10-55 μm.

[0013] In the above technical solution of the present invention, by controlling the particle size of the functional alloy spherical powder between 10-55 μm, the surface roughness of the cladding layer formed after the functional alloy spherical powder is clad can be reduced to ensure that the surface roughness of the cladding layer is between 10-50 μm.

[0014] Furthermore, in the manufacturing method of the present invention, the laser power used in the cladding is 1-6 kW, the laser spot diameter is 0.8-5.0 mm, and the cladding linear speed is 1000-20000 mm / min.

[0015] In the above-mentioned technical solution of the present invention, when using a laser to perform ultra-high-speed cladding of functional alloy spherical powder on the inner wall of a substrate tube, the laser power, laser spot diameter, and cladding linear speed are the most important parameters that require the most control. The laser power used for cladding is preferably controlled within a range of 1-6kW to ensure cladding efficiency while preventing equipment overheating. The cladding linear speed can be selected within the range of 1000-20000 mm / min, depending on the thickness of the cladding layer. To balance production efficiency and cladding uniformity, the laser spot diameter can be controlled between 0.8-5.0 mm.

[0016] Furthermore, in the manufacturing method of the present invention, the laser cladding is performed under argon protection, and the oxygen content is controlled to be less than 50 ppm.

[0017] Furthermore, in the manufacturing method of the present invention, during the cladding process, the powder feeding speed of the functional alloy spherical powder is controlled to be 0.2-10.0 g / min.

[0018] In the present invention, in order to balance production efficiency and cladding uniformity, the powder feeding rate of the spherical powder can be preferably controlled to 0.2-10.0 g / min, the thickness of the single-pass deposition can be controlled to 0.3-0.5 mm, and the overlap rate can be controlled to 30%-80%. In particular, during laser cladding, the combined effects of forced convection caused by the surface tension gradient and wettability result in a single-pass cladding layer that is convex rather than flat. If the cladding layers are not overlapped, the effective thickness of the cladding layer at the junction of different passes is 0, and the cladding layer surface will appear uneven and rough. In addition, it should be noted that the overlap rate describes the degree of overlap between adjacent cladding layers in laser cladding, and is defined as the ratio of the overlap width between adjacent cladding layers to the width of the single-pass cladding layer.

[0019] Furthermore, in the manufacturing method of the present invention, during the cladding process, the thickness of the single-pass deposition is 0.3-0.5 mm.

[0020] Furthermore, in the manufacturing method of the present invention, when laser cladding is performed to form the cladding layer, the overlap rate is controlled to be 30%-80%.

[0021] Furthermore, in the manufacturing method of the present invention, a cladding layer with a thickness of 0.3-1.0 mm is formed on the inner wall of the substrate tube by single-pass or multi-pass deposition.

[0022] Furthermore, in the manufacturing method of the present invention, during the cladding process, the dilution rate is controlled to be 1wt%-5wt%.

[0023] Furthermore, in the manufacturing method of the present invention, the functional alloy spherical powder is made of a functional alloy, and the functional alloy includes one of the following: martensitic stainless steel, duplex stainless steel, austenitic stainless steel or nickel-based alloy.

[0024] In the above technical solution of the present invention, the functional alloy used in the functional alloy spherical powder to meet the performance requirements of high resistance to H2S and CO2 corrosion can be selected from martensitic stainless steel, duplex stainless steel, austenitic stainless steel, or nickel-based alloys, etc., as required. Of course, in some other embodiments, other functional alloys can also be selected according to specific requirements.

[0025] Accordingly, another object of the present invention is to obtain a bimetallic metallurgical composite pipeline pipe, which has a low cost, can meet the performance requirements of high resistance to H2S and CO2 corrosion, and has considerable mechanical properties. It can be effectively applied to the oil and gas industry and has a very broad market prospect.

[0026] In order to achieve the above-mentioned object, the present invention discloses a bimetallic metallurgical composite pipeline pipe, which is manufactured by the manufacturing method of the bimetallic metallurgical composite pipeline pipe of the present invention.

[0027] The manufacturing method of the bimetallic metallurgical composite line pipe and the bimetallic metallurgical composite line pipe of the present invention have the following advantages and beneficial effects compared with the prior art:

[0028] The manufacturing method of the bimetallic metallurgical composite line pipe of the present invention is simple to implement and has low production costs. The manufacturing method can effectively produce bimetallic metallurgical composite line pipe. The produced bimetallic metallurgical composite line pipe can fully achieve metallurgical bonding, meet the performance requirements of high resistance to H2S and CO2 corrosion, and have considerable mechanical properties. The bimetallic metallurgical composite line pipe can meet the transportation requirements of oil and gas fields containing H2S and CO2 corrosive media, and is used for oil and gas transportation containing H2S and CO2 corrosive media, and has a very broad market prospect.

[0029] In the manufacturing method described herein, an ultra-high-speed laser is used to clad the inner wall of a substrate tube with spherical functional alloy powder, achieving a complete metallurgical bond and preventing flaking or delamination during service. During the cladding process, the laser cladding process causes minimal damage to the substrate tube and does not compromise its sulfur resistance. The cladding layer thickness can be controlled to between 0.3 and 1.0 mm, with a spherical powder utilization rate exceeding 90%, significantly reducing the use of expensive functional alloys. During cladding, the cladding line speed can be controlled to between 1,000 and 20,000 mm / min, and the dilution rate can be maintained between 1 and 5 wt% to ensure a dense structure in the cladding layer.

[0030] The manufacturing method of the present invention can realize the production of bimetallic metallurgical composite pipeline pipe while controlling low production costs. The resulting bimetallic metallurgical composite pipeline pipe has low cost and excellent mechanical properties and corrosion resistance. Its cost is only 1 / 5 to 1 / 2 of that of similar functional alloy pipeline pipes of the same specifications, while its corrosion resistance can reach the level of similar functional alloy pipeline pipes, and its mechanical properties meet the API 5L standard. BRIEF DESCRIPTION OF THE DRAWINGS

[0031] Figure 1 A schematic diagram of the composite interface structure of the cladding layer formed by cladding the inner wall of the substrate tube according to the present invention is shown. DETAILED DESCRIPTION

[0032] The manufacturing method of the bimetallic metallurgical composite line pipe and the bimetallic metallurgical composite line pipe of the present invention will be further explained and illustrated below in conjunction with specific embodiments. However, such explanation and illustration do not constitute an undue limitation to the technical solution of the present invention.

[0033] In the present invention, a method for manufacturing a bimetallic metallurgical composite pipeline pipe is provided. The bimetallic metallurgical composite pipeline pipe manufactured by this manufacturing method can not only meet the performance requirements of high resistance to H2S and CO2 corrosion but also has considerable mechanical properties, and can be effectively applied to the oil and gas industry.

[0034] In order to further illustrate the advantages of the bimetallic metallurgical composite line pipe of the present invention, the inventors designed and implemented the technical solutions of the following Examples 1-8 to illustrate the present invention.

[0035] Examples 1-8

[0036] In the present invention, taking the 114*7 mm specification as an example, Examples 1-8 can use sulfur-resistant line pipes of different steel grades, BQS and X60QS, as base pipes, and use different functional alloys: martensitic stainless steel Super13Cr, duplex stainless steel S32001, austenitic stainless steel S31603, and nickel-based alloy NO8825, as cladding layer materials, respectively. The above functional alloys all need to be made into spherical powders with a particle size of 10-55 μm. The specific material selection is detailed in Table 1.

[0037] Table 1.

[0038] serial number Base pipe Functional alloy materials Example 1 BQS Super13Cr Example 2 BQS S32001 Example 3 BQS S31603 Example 4 BQS NO8825 Example 5 X60QS Super13Cr Example 6 X60QS S32001 Example 7 X60QS S31603 Example 8 X60QS NO8825

[0039] In the present invention, the chemical element compositions of the above-mentioned functional alloy materials are listed in Table 2 below.

[0040] Table 2. (wt%, the balance is Fe and other inevitable impurities)

[0041] Functional alloys C Si Mn S P Cr Ni Mo Cu Super13Cr ≤0.03 0.2-0.5 0.3-0.5 - - 12.0-13.3 4.5-6.0 1.5-3.0 ≤0.25 S32001 ≤0.03 ≤1.0 4.0-6.0 ≤0.03 ≤0.04 19.5-21.5 1.0-3.0 ≤0.6 ≤1.0 S31603 ≤0.03 ≤1.0 ≤2.0 ≤0.03 ≤0.045 16.0-18.0 10.0-14.0 2.0-3.0 - NO8825 ≤0.05 - - - - 19.5-23.5 38.0-46.0 2.5-3.5 1.5-3.0

[0042] After the material selection is completed, each embodiment is protected by argon gas, the oxygen content is controlled to be less than 50ppm, and the spherical powder of the functional alloy material corresponding to each embodiment is clad on the inner wall of the substrate tube by ultra-high-speed laser. The laser power used for cladding is controlled to be 1-6kW, the laser spot diameter is 0.8-5.0mm, the cladding line speed is 1000-20000mm / min, and the powder feeding rate of the functional alloy spherical powder is controlled to be 0.2-10.0g / min.

[0043] During the cladding process, spherical powder can be accumulated to form a cladding layer on the inner wall of the substrate tube, and the dilution rate can be controlled to be 1wt%-5wt%. The thickness of a single-pass accumulation can be controlled to be 0.3-0.5mm. When laser cladding is used to form the cladding layer, the overlap rate can be controlled to be 30%-80%. The inner wall of the substrate tube can be deposited in a single pass or layer by layer in multiple passes according to needs to form a cladding layer with a thickness of 0.3-1.0mm.

[0044] Table 3-1 and Table 3-2 list the process parameters of the bimetallic metallurgical composite line pipes of Examples 1-8 during the above manufacturing process.

[0045] Table 3-1.

[0046]

[0047] Table 3-2.

[0048]

[0049] In Table 3-2 above, the single-pass buildup thickness of Example 4 is expressed as "0.3 / 0.3," which can be understood as Example 4 using two-layer multi-pass buildup, with the first pass buildup thickness being 0.3 mm and the second pass buildup thickness being 0.3 mm. Accordingly, the relevant data for Examples 5-8 are understood the same as above and will not be repeated here.

[0050] The finished bimetallic composite linepipes of Examples 1-8, produced after the above-described processes, were sampled to obtain samples of each embodiment. In the present invention, samples of Super13Cr, S32001, S31603, and NO8825 functional alloy linepipes were also collected and used as Comparative Examples 1-4 for comparison with the bimetallic composite linepipe samples of Examples 1-8, thereby evaluating the stress corrosion cracking (SCC) resistance of the bimetallic composite linepipes of Examples 1-8.

[0051] In the present invention, the stress corrosion cracking (SCC) resistance of the functional alloy linepipes of Examples 1-8 and Comparative Examples 1-4 can be evaluated according to the ISO 7539-2 standard four-point bending method. It should be noted that during the testing process, the applied stress for Examples 1-8 can be controlled to be the yield strength of each sulfur-resistant base pipe; and the applied stress for Comparative Examples 1-4 can be controlled to be the yield strength of each functional alloy.

[0052] In addition, during the test, it is necessary to control the test temperature and the liquid medium Cl - The content, pH, CO2 partial pressure, H2S partial pressure and total pressure are controlled to simulate the corrosive working environment. In the present invention, the test simulates four simulated corrosive working environments. The detailed description of these four simulated corrosive working environments is shown in Table 4 below.

[0053] Table 4.

[0054]

[0055] The linepipe samples of Examples 1-8 and Comparative Examples 1-4 were tested under the four simulated corrosion conditions described above to obtain SCC resistance test results for the bimetallic metallurgical composite linepipes of Examples 1-8 and the functional alloy linepipes of Comparative Examples 1-4. The relevant test results are listed in Table 5 below.

[0056] Table 5 lists the SCC resistance test results of the bimetallic metallurgical composite line pipes of Examples 1-8 and the functional alloy line pipes of Comparative Examples 1-4.

[0057] Table 5.

[0058]

[0059] In Table 5, "√" indicates no stress corrosion cracking, and "×" indicates stress corrosion cracking. Table 5 shows that the bimetallic metallurgical composite linepipes of Examples 1-8, obtained using the manufacturing method of the bimetallic metallurgical composite linepipe of the present invention, have stress corrosion cracking (SCC) resistance comparable to that of similar functional alloy linepipes (Comparative Examples 1-4), while achieving a production cost lower than that of similar functional alloy linepipes.

[0060] In addition, further reference to Table 5 shows that under different corrosion conditions, the stress corrosion cracking resistance of pipelines with different functional alloys / bimetallic metallurgical composite pipelines with different functional alloys as cladding layers varies. Users can choose to use them based on actual conditions such as working conditions and cost.

[0061] Thus, the manufacturing method of the bimetallic metallurgical composite line pipe of the present invention has a low production cost. The manufacturing method can effectively produce bimetallic metallurgical composite line pipe. The produced bimetallic metallurgical composite line pipe can not only meet the performance requirements of high resistance to H2S and CO2 corrosion but also has considerable mechanical properties. It can be effectively applied to the oil and gas industry and has a very broad market prospect.

[0062] Figure 1 A schematic diagram of the composite interface structure of the cladding layer formed by cladding the inner wall of the substrate tube according to the present invention is shown.

[0063] like Figure 1 As shown, in the bimetallic metallurgical composite line pipe of the present invention, there is no delamination between the base pipe and the cladding layer formed by the functional alloy spherical powder, and the cladding is performed by ultra-high-speed laser to achieve complete metallurgical bonding.

[0064] It should be noted that the combination of the various technical features in this case is not limited to the combination described in the claims of this case or the combination described in the specific embodiments. All technical features recorded in this case can be freely combined or combined in any way unless there is a contradiction between them.

[0065] It should also be noted that the embodiments listed above are merely specific embodiments of the present invention. Obviously, the present invention is not limited to the above embodiments, and similar changes or modifications made therefrom that can be directly derived from or easily conceived by those skilled in the art based on the disclosure of the present invention are intended to fall within the scope of protection of the present invention.

Claims

1. A method for manufacturing a bimetallic metallurgical composite line pipe, characterized in that: Including steps: The sulfur-resistant line pipe is used as a base pipe, and functional alloy spherical powder is laser clad on the inner wall of the base pipe to form a cladding layer, the surface roughness of the cladding layer is 10-50 μm; the particle size of the functional alloy spherical powder is 10-55 μm.

2. The manufacturing method according to claim 1, wherein The laser power used in the cladding is 1-6kW, the laser spot diameter is 0.8-5.0mm, and the cladding line speed is 1000-20000mm / min.

3. The manufacturing method according to claim 1, wherein: Laser cladding is carried out under argon protection, and the oxygen content is controlled to be less than 50ppm.

4. The manufacturing method according to claim 1, wherein: During the cladding process, the feeding speed of the functional alloy spherical powder is controlled to be 0.2-10.0 g / min.

5. The manufacturing method according to claim 1, wherein: During the cladding process, the thickness of the single-pass accumulation is 0.3-0.5mm.

6. The manufacturing method according to claim 1, wherein: When laser cladding is performed to form a cladding layer, the overlap rate is controlled to be 30%-80%.

7. The manufacturing method according to claim 1, wherein: A cladding layer with a thickness of 0.3-1.0 mm is formed on the inner wall of the base pipe by single-pass or multi-pass deposition.

8. The manufacturing method according to claim 1, wherein: During the cladding process, the dilution rate is controlled to be 1wt%-5wt%.

9. The manufacturing method according to claim 1, wherein: The functional alloy spherical powder is made of a functional alloy, and the functional alloy includes one of the following: martensitic stainless steel, duplex stainless steel, austenitic stainless steel or nickel-based alloy.

10. A bimetallic metallurgical composite line pipe, manufactured by the manufacturing method according to any one of claims 1 to 9.

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