High-toughness nickel-aluminum bronze alloy and efficient forming method and application thereof

Abstract

The invention discloses a high-toughness nickel-aluminum bronze alloy and an efficient forming method and application thereof. The invention belongs to the field of nickel-aluminum bronze alloy materials. The invention aims to provide a high-toughness nickel-aluminum bronze alloy and an efficient forming method and application thereof. The method comprises the following steps: carrying out three-dimensional modeling; a nickel-aluminum bronze alloy wire and a nickel-aluminum bronze alloy plate are used as a wire material and a substrate for printing respectively, electron beam fuse deposition is carried out under the vacuum condition, and the interlayer cooling temperature is lower than 100 DEG C; and keeping the temperature at 580-620 DEG C for 50-70 minutes, and then cooling to room temperature in air. According to the method provided by the invention, near-net rapid prototyping of the nickel-aluminum bronze alloy can be realized, the continuous deposition efficiency reaches 3.2 kg / h, and the nickel-aluminum bronze alloy has excellent mechanical properties and is applied to the fields of ocean engineering, shipbuilding, chemical equipment, aerospace and petroleum and natural gas.

Description

Technical Field

[0001] The present invention belongs to the field of nickel-aluminum bronze alloy materials, and particularly relates to a high-strength and tough nickel-aluminum bronze alloy, an efficient forming method thereof, and applications thereof. Background Art

[0002] Nickel-aluminum bronze alloy is a copper alloy mainly composed of aluminum, iron, nickel, and manganese. Nickel-aluminum bronze alloy has excellent corrosion resistance, high strength, high hardness, and good fatigue resistance, and is widely used in the fields of ocean engineering, shipbuilding, chemical equipment, aerospace, and oil and gas, etc.

[0003] In traditional manufacturing methods, there are problems such as coarse grains and easy generation of defects (such as pores and shrinkage cavities) in cast nickel-aluminum bronze alloys, which affect the mechanical properties and service life of the materials. Although forging nickel-aluminum bronze can improve the microstructure, the process is complex and the processing cost is high. At the same time, the ability to manufacture the shape of complex parts is limited, and the manufacturing flexibility is poor.

[0004] As an emerging technology, additive manufacturing has advantages such as high material utilization rate, strong complex structure manufacturing ability, and high process flexibility. Related research includes processes such as laser powder bed fusion, electron beam powder bed fusion, and laser directed energy deposition. Although these technologies can achieve high-precision manufacturing of high-strength nickel-aluminum bronze alloys, their deposition efficiency is low, and it is usually difficult to meet the requirements of high-efficiency production of large parts. Arc additive manufacturing has a high efficiency, but due to the oxidation risk in the process, it is difficult to ensure the mechanical properties and reliability of the materials. In addition, the heat treatment process for additive manufacturing nickel-aluminum bronze parts still uses the heat treatment process of alloys manufactured by traditional manufacturing methods, resulting in non-optimized microstructure of the prepared parts, and thus affecting the mechanical properties. Summary of the Invention

[0005] In order to overcome the above technical defects, the present invention provides a high-strength and tough nickel-aluminum bronze alloy, an efficient forming method thereof, and applications thereof.

[0006] The technical solution of the present invention is as follows:

[0007] One of the purposes of the present invention is to provide an efficient forming method of a high-strength and tough nickel-aluminum bronze alloy, and the method is carried out according to the following steps:

[0008] S1: Three-dimensional modeling and importing the generated printing information into the control system of an electron beam wire deposition device;

[0009] S2: Using nickel-aluminum bronze alloy wire and nickel-aluminum bronze alloy plate as the printing wire and substrate respectively, and carrying out electron beam wire deposition under vacuum conditions. The deposition process parameters: the acceleration voltage U is 50 - 70 kV, the focusing current I f is 1020 - 1040 mA, the wire feeding speed Vfeed is 3.0 - 4.2 m / min, and the beam current density I b is 50 - 60 mA, and the printing speed V print is 500 - 700 mm / min, and the interlayer cooling temperature < 100 °C;

[0010] S3: Take out the printed and formed parts from the vacuum chamber, put them into a heat treatment furnace for heat treatment, hold at 580 - 620 °C for 50 - 70 min, and cool to room temperature.

[0011] Further defined, the wire material in S2 is pickled, soaked in alcohol, and dried in sequence before deposition.

[0012] Further defined, the substrate in S2 is polished, wiped with alcohol, and dried in sequence before deposition.

[0013] Further defined, the alloy wire composition in S2 is SCu6328, and the plate composition is C95800.

[0014] Further defined, the vacuum degree during deposition in S2 < 7×10 -2 MPa.

[0015] Further defined, the acceleration voltage U in S2 is 60 kV, the focusing current I f is 1030 mA, and the wire feeding speed V feed is 3.6 m / min, and the beam current density I b is 55 mA, and the printing speed V print is 600 mm / min.

[0016] Further defined, hold at 600 °C for 60 min in S3.

[0017] Further defined, cool to room temperature in air in S3.

[0018] The second object of the present invention is to provide a high-strength and tough nickel-aluminum bronze alloy prepared by the above method.

[0019] The third object of the present invention is to provide an application of the high-strength and tough nickel-aluminum bronze alloy prepared by the above method in the fields of ocean engineering, shipbuilding, chemical equipment, aerospace, and oil and gas.

[0020] Compared with the prior art, the advantages of the present invention are:

[0021] The method provided by the present invention can realize near-net rapid forming of nickel-aluminum bronze alloy, and the continuous deposition efficiency reaches 3.2 kg per hour;

[0022] The nickel-aluminum bronze alloy parts prepared by the method provided by the present invention have excellent mechanical properties. The microhardness is 250.35 ± 2.30 HV0.5 The yield strength is 534 MPa, the tensile strength is 839 MPa, and the elongation after fracture is 18.6%. Description of the Drawings

[0023] Figure 1 Physical diagram of the nickel-aluminum bronze alloy obtained in the example;

[0024] Figure 2 Grain boundary distribution diagrams of the example, Comparative Example 1, and Comparative Example 2; where (a) is the example, (b) is Comparative Example 1, and (c) is Comparative Example 2;

[0025] Figure 3 Tensile stress-strain curves of the example, Comparative Example 1, and Comparative Example 2;

[0026] Figure 4 Hardness comparison diagrams of the example, Comparative Example 1, and Comparative Example 2;

[0027] Figure 5 Microstructure morphologies of the example and Comparative Examples 3 and 4; where (a) is the example, (b) is Comparative Example 3, and (c) is Comparative Example 4;

[0028] Figure 6 Tensile stress-strain curves of the example and Comparative Examples 3 and 4;

[0029] Figure 7 Hardness comparison diagrams of the example and Comparative Examples 3 and 4;

[0030] Figure 8 Hardness comparison diagram of the example and Comparative Example 5. Detailed Description of the Invention

[0031] In order to make the objectives, technical solutions, and advantages of the present invention clearer, the present invention will be further described in detail below with reference to examples. It should be understood that the specific examples described herein are only used to explain the present invention and are not used to limit the present invention.

[0032] The experimental methods used in the following examples are all conventional methods unless otherwise specified. The materials, reagents, methods, and instruments used are all conventional materials, reagents, methods, and instruments in the art unless otherwise specified, and those skilled in the art can obtain them through commercial channels.

[0033] The terms "comprising", "including", "having", "containing", or any other variation thereof used in the following examples are intended to cover non-exclusive inclusion. For example, a composition, step, method, article, or device containing the listed elements does not necessarily have to be limited to those elements, but may include other elements not expressly listed or elements inherent to such composition, step, method, article, or device.

[0034] When an equivalent, concentration, or other value or parameter is expressed as a range, a preferred range, or a range defined by a series of upper preferred values and lower preferred values, this should be understood to specifically disclose all ranges formed by any pairing of any range upper limit or preferred value with any range lower limit or preferred value, regardless of whether the range is disclosed individually. For example, when the range "1 to 5" is disclosed, the described range should be interpreted to include ranges "1 to 4", "1 to 3", "1 to 2", "1 to 2 and 4 to 5", "1 to 3 and 5", etc. When a numerical range is described herein, unless otherwise stated, the range is intended to include its end values and all integers and fractions within the range. In the specification and claims of this application, range limitations can be combined and / or interchanged, and if not otherwise stated, these ranges include all sub-ranges contained therein.

[0035] The high-efficiency forming method of the high-strength and tough nickel-aluminum bronze alloy in this example is carried out according to the following steps:

[0036] (1) Perform three-dimensional modeling according to the shape of the target component. In this example, the target is to prepare a block alloy with a length, width, and height of 100 mm × 50 mm × 10 mm, and generate an STL file of the printing information;

[0037] (2) Pickle the commercial nickel-aluminum bronze alloy wire with a diameter of 1.6 mm (SCu6328 (CuAl9Ni5Fe3Mn2)), remove the surface oxide film, and then soak and clean it with alcohol to ensure that there are no oil and impurity contaminants on the surface of the nickel-aluminum bronze alloy wire;

[0038] (3) Use a commercial C95800 nickel-aluminum bronze plate with a size of 150 mm × 80 mm × 12 mm as the substrate, sand it until the surface is smooth and clean, and then wipe the surface with alcohol to remove the oil and impurity contaminants on the substrate surface;

[0039] (4) Place both the nickel-aluminum bronze alloy wire and the nickel-aluminum bronze plate in a drying oven at 60 °C for drying treatment, and keep warm for 30 min to remove the moisture inside the wire and the plate;

[0040] (5) Install the treated nickel-aluminum bronze alloy wire on the wire feeding mechanism of the electron beam wire and arc additive manufacturing equipment, and clamp the treated C95800 nickel-aluminum bronze plate on the motion system inside the vacuum chamber of the electron beam wire and arc additive manufacturing equipment;

[0041] (6) Start the electron beam wire and arc additive manufacturing equipment, start the vacuum pump system to evacuate the vacuum chamber, the electron gun, and the wire feeding system. Wait until the vacuum degree of the vacuum chamber of the electron beam wire and arc additive manufacturing equipment reaches the use requirement (7 × 10 -2 Pa);

[0042] (7) Import the printing information generated in step (1) into the automatic control system of the electron beam fused deposition equipment, and set the following processing parameters: the acceleration voltage U is 60 kV, and the focusing current I f is 1030 mA, and the wire feeding speed V feed is 3.6 m / min, and the printing speed V print is 600 mm / min, and the beam current density I b is 55 mA. Control the interlayer cooling temperature by controlling the interlayer cooling time, and perform the next layer deposition when the temperature of the formed layer is lower than 100 °C;

[0043] (8) According to the control program in step (7), complete the rapid preparation of nickel-aluminum bronze alloy by electron beam fused deposition to obtain nickel-aluminum bronze alloy by electron beam fused additive manufacturing;

[0044] (9) Take out the nickel-aluminum bronze alloy obtained in step (8) and place it in a heat treatment furnace. Set the automatic control program of the heat treatment furnace to heat up from room temperature to 600 °C at a rate of 10 °C / min and hold for 1 h at 600 °C.

[0045] (10) Execute the heat treatment automatic control program in step (9). After the heat preservation is completed, take out the nickel-aluminum bronze alloy and let it cool naturally in the air. The physical diagram of the obtained nickel-aluminum bronze alloy is as Figure 1 shown.

[0046] Comparative Example 1:

[0047] The difference between this comparative example and the embodiment of the present invention is that: in step (7), the temperature of the formed layer is set to be lower than 200 °C and higher than 100 °C.

[0048] Comparative Example 2:

[0049] The difference between this comparative example and the embodiment of the present invention is that: in step (7), the interlayer cooling time is not set.

[0050] Comparative Example 3:

[0051] The difference between this comparative example and the embodiment of the present invention is that: steps (9)-(10) are omitted, that is, no heat treatment is performed.

[0052] Comparative Example 4:

[0053] The difference between this comparative example and the embodiment of the present invention is that: in step (9), the automatic control program of the heat treatment furnace is set to heat up from room temperature to 675 °C at a rate of 10 °C / min and hold for 6 hours at 675 °C. Holding for 6 hours at 675 °C is considered as the preferred heat treatment process for traditional cast alloys.

[0054] Comparative Example 5:

[0055] The differences between this comparative example and the embodiments of the present invention are as follows: In step (9), the automatic control program of the heat treatment furnace is set to increase the temperature from room temperature to 550 °C, 600 °C, and 650 °C at a rate of 10 °C / min respectively. Keep warm for 15 min, 30 min, 60 min, and 120 min at 550 °C and 650 °C respectively, and keep warm for 15 min, 30 min, and 120 min at 600 °C respectively.

[0056] The grain boundary distribution diagrams of the embodiments, comparative example 1, and comparative example 2 are as Figure 2 shown. The average grain size is obtained by statistically averaging the major diameters of the equivalent ellipses of the grains. The average grain size of the embodiment is 7.6 μm, the average grain size of comparative example 1 is 14.5 μm, and the average grain size of comparative example 2 is 19.1 μm. Effectively refining the grains by controlling the interlayer cooling temperature helps to obtain excellent mechanical properties.

[0057] The tensile stress-strain curves of the embodiments, comparative example 1, and comparative example 2 are as Figure 3 shown. The yield strength of the embodiment is 534 MPa, the tensile strength is 839 MPa, and the elongation after fracture is 18.6%. The yield strength of comparative example 1 is 412 MPa, the tensile strength is 784 MPa, and the elongation after fracture is 22.9%. The yield strength of comparative example 2 is 387 MPa, the tensile strength is 756 MPa, and the elongation after fracture is 25.7%. The embodiment exhibits the optimal yield strength and tensile strength and maintains an excellent elongation rate.

[0058] The hardness comparison of the embodiments, comparative example 1, and comparative example 2 is as Figure 4 shown. The hardness of the embodiment is 250.35 ± 2.30 HV 0.5 , the hardness of comparative example 1 is 224.97 ± 1.98 HV 0.5 , and the hardness of comparative example 2 is 219.60 ± 2.12 HV 0.5 . The embodiment has the highest hardness.

[0059] The microstructural morphologies of the embodiment, comparative example 3, and comparative example 4 are as Figure 5 shown. Fine and dense precipitates are formed in the embodiment; only a small number of precipitates exist in comparative example 3; the precipitates in comparative example 4 aggregate and grow. The fine and dense precipitates in the embodiment are beneficial to obtaining excellent strength and hardness.

[0060] The tensile stress-strain curves of the embodiment, comparative example 3, and comparative example 4 are as Figure 6As shown. The yield strength of the example is 534 MPa, the tensile strength is 839 MPa, and the elongation after fracture is 18.6%. The yield strength of Comparative Example 3 is 464 MPa, the tensile strength is 762 MPa, and the elongation after fracture is 23.6%. The yield strength of Comparative Example 4 is 479 MPa, the tensile strength is 778 MPa, and the elongation after fracture is 21.9%. The example exhibits the optimal yield strength and tensile strength and maintains an excellent elongation rate.

[0061] The hardness comparison between the example and Comparative Example 3 and Comparative Example 4 is as Figure 7 shown. The hardness of the example is 250.35 ± 2.30 HV 0.5 , the hardness of Comparative Example 3 is 220.06 ± 1.53 HV 0.5 , the hardness of Comparative Example 4 is 226.42 ± 2.06 HV 0.5 . The example has the highest hardness.

[0062] The hardness comparison between the example and Comparative Example 5 is as Figure 8 shown. The example corresponding to holding at 600 °C for 60 min has a high hardness and a short holding time.

[0063] As mentioned above, only the preferred specific embodiments of the present invention are described. These specific embodiments are different implementation manners based on the overall concept of the present invention, and the protection scope of the present invention is not limited thereto. Any changes or substitutions that can be easily thought of by those skilled in the art within the technical scope disclosed by the present invention should be covered by the protection scope of the present invention. Therefore, the protection scope of the present invention should be subject to the protection scope of the claims.

Claims

1. An efficient forming method for a high-strength and tough nickel-aluminum bronze alloy, characterized in that, The method described above: S1: Conduct three-dimensional modeling and import the generated printing information into the control system of the electron beam wire deposition equipment; S2: Using nickel-aluminum bronze alloy wire and nickel-aluminum bronze alloy plate as the printing wire and substrate respectively, electron beam wire and arc additive manufacturing is carried out under vacuum conditions. The deposition process parameters are as follows: the acceleration voltage U is 50 - 70 kV, the focusing current I f is 1020 - 1040 mA, the wire feeding speed V feed is 3.0 - 4.2 m / min, the beam current density I b is 50 - 60 mA, the printing speed V print is 500 - 700 mm / min, and the interlayer cooling temperature < 100 °C; S3: Take out the printed parts from the vacuum chamber and put them into a heat treatment furnace for heat treatment, keep them at 580 - 620 °C for 50 - 70 min, and then cool them to room temperature.

2. The method according to claim 1, characterized in that, In S2, the wire is pickled, soaked in alcohol and dried in sequence before deposition.

3. The method according to claim 1, wherein In S2, the substrate is polished, wiped with alcohol and dried in sequence before deposition.

4. The method according to claim 1, wherein In S2, the alloy wire composition is SCu6328, and the plate composition is C95800.

5. The method according to claim 1, characterized in that, The vacuum degree during deposition in S2 < 7×10 -2 MPa.

6. The method according to claim 1, characterized in that, In S2, the acceleration voltage U is 60 kV, the focusing current I f is 1030 mA, and the wire feeding speed V feed is 3.6 m / min, the beam current density I b is 55 mA, and the printing speed V print is 600 mm / min.

7. The method according to claim 1, characterized in that In S3, keep at 600 °C for 60 min.

8. The method according to claim 1, characterized in that, In S3, cool to room temperature in air.

9. A high-strength and tough nickel-aluminum bronze alloy prepared by the method according to any one of claims 1 - 8.

10. Application of the high-strength and tough nickel-aluminum bronze alloy according to claim 9 in the fields of ocean engineering, shipbuilding, chemical equipment, aerospace and oil and gas.

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