Preparation method of metal diaphragm of diaphragm compressor

Abstract

The invention relates to a preparation method of a diaphragm compressor metal diaphragm, the material of the metal diaphragm is GH4169, and the component range of the GH4169 is C: 0.015-0.06; 17 to 21 parts of Cr; 4.75 to 5.5 parts of Nb; 2.8 to 3.3% of Mo; 0.3 to 0.7 part of Al; 0.75 to 1.15 parts of Ti; 0 to 0.35 percent of Si; ni: the balance; the thickness of the GH4169 ranges from 0.3 mm to 0.8 mm; the method comprises the following steps that S1, the metal diaphragm is placed in a resistance furnace to be subjected to solution treatment; s2, carrying out rapid oil quenching treatment on the metal diaphragm subjected to solution treatment in the step S1; and S3, the metal diaphragm subjected to rapid oil treatment in the S2 is subjected to aging treatment. The metal diaphragm prepared through the method has the advantages of being high in tensile strength, good in toughness, small in grain size uniform distribution range and high in austenite content.

Description

Technical Field

[0001] The present disclosure relates to the field of hydrogen energy, and specifically, to a method for preparing a metal diaphragm of a diaphragm compressor. Background Art

[0002] A metal diaphragm diaphragm compressor changes the volume of the air chamber by driving the diaphragm to deform through the piston compressing the oil in the oil chamber, so as to achieve the purpose of compressing the gas in the air chamber. The diaphragm is the most critical and most easily damaged component during the operation of the diaphragm compressor. The main forms of damaged diaphragms are distortion, collapse, wear cracks, and mechanical fatigue. The metal diaphragm undergoes flexural deformation under the action of alternating loads due to the pressure difference between the liquid and gas, resulting in fatigue failure. There are many factors affecting the diaphragm life, such as whether the mechanical properties of the diaphragm material are excellent; the surface finish of the diaphragm is not high; the residual impurities on the surface are likely to cause stress concentration; the diaphragm is too thin and easy to break, and too thick results in poor flexural deformation ability.

[0003] The article "Shi Ting, Li Haisheng, Wang Jiansong, et al. Research on the Interlayer Contact Mechanics Behavior of the Metal Diaphragm of the Diaphragm Compressor. Fluid Machinery, 2016, 44(10): 5." points out that the main reason for the failure of the metal diaphragm is the insufficient maximum tensile stress in the slip zone. At the same time, the article "Theoretical Analysis of the Diaphragm Rupture of the Original Diaphragm Design" also points out that the insufficient radial stress of the diaphragm is also the main reason for gas rupture. Although the patent document CN110566444A provides a method for surface modification of the metal diaphragm, the material of the diaphragm substrate has not changed. During long-term use, the surface coating will fall off, resulting in a greatly increased probability of diaphragm failure. The article "Wang Yan, Lin Lin, Shao Wenzhu, et al. Influence of Solution Treatment on the Microstructure and Properties of GH4169 Alloy. Transactions of Materials and Heat Treatment, 2007, 28(B08): 4." presents the influence of different treatment conditions on the grain size of GH4169, but does not clarify whether the grains are completely austenite phase, nor does it propose its application in a hydrogen diaphragm compressor. The article "Jakob Tatiana Mishurova, Tobias Fritsch, et.al. On the influence of heat treatment on microstructure and mechanical behavior of laser powder bed fused Inconel 718, Journal Pre-proof" describes the influence of different treatment temperatures and holding times on the grain size and mechanical properties of the material, but does not clearly indicate the range of grain size and the content of austenite phase.

[0004] For a hydrogen diaphragm compressor, since the gas-side diaphragm in contact with hydrogen is in a high-pressure hydrogen environment for a long time, hydrogen embrittlement failure often occurs due to the accumulation of hydrogen after it penetrates into the diaphragm. Summary of the Invention

[0005] The object of the present disclosure is to solve the problem of hydrogen embrittlement failure of the gas-side diaphragm of a hydrogen diaphragm compressor.

[0006] To achieve the above object, the present disclosure provides a method for preparing a metal diaphragm of a diaphragm compressor. The material of the metal diaphragm of the diaphragm compressor is GH4169, and the composition range of GH4169 is: C: 0.015 - 0.06; Cr: 17 - 21; Nb: 4.75 - 5.5; Mo: 2.8 - 3.3; Al: 0.3 - 0.7; Ti: 0.75 - 1.15; Si: 0 - 0.35; Ni: the balance;

[0007] The thickness of the metal diaphragm is 0.3 - 0.8 mm;

[0008] The method includes the following steps:

[0009] S1. Place the GH4169 blank in a resistance furnace for solution treatment to obtain the material after solution treatment;

[0010] S2. Perform oil quenching treatment on the material after solution treatment to obtain the material after oil quenching treatment;

[0011] S3. Perform aging treatment on the material after oil quenching treatment to obtain the metal diaphragm of the diaphragm compressor.

[0012] Optionally, in step S1, the solution treatment includes a heating-up treatment. The heating-up rate of the heating-up treatment is 5 °C / min - 10 °C / min, and the time is 100 - 204 min.

[0013] Optionally, in step S1, the solution treatment further includes an isothermal treatment. The temperature of the isothermal treatment is 1000 - 1020 °C, and the time is 1 - 2 h.

[0014] Optionally, in step S2, the conditions of the oil quenching treatment include: the treatment temperature is 20 - 40 °C, and the time is 10 - 50 min.

[0015] Optionally, in step S3, the aging treatment includes an annealing treatment. The temperature of the annealing treatment is 700 - 750 °C, and the time is 1 - 3 h.

[0016] Optionally, in step S3, the aging treatment further includes a tempering treatment. The temperature of the tempering treatment is 600 - 650 °C, and the time is 1 - 3 h.

[0017] Optionally, the proportion of the austenite phase in the metal diaphragm of the diaphragm compressor is 98 - 99.7%.

[0018] Optionally, the tensile strength of the metal diaphragm of the diaphragm compressor is 1125 - 1357 MPa.

[0019] Optionally, the elongation at break of the metal diaphragm of the diaphragm compressor is 25.7 - 36.3%.

[0020] Optionally, the grain size range of the metal diaphragm of the diaphragm compressor is 10 - 25 μm.

[0021] Through the above technical solution, the metal diaphragm of the diaphragm compressor prepared by this method has the advantages of high tensile strength, good toughness, small and uniform distribution range of grain size, and high austenite content.

[0022] Other features and advantages of the present disclosure will be described in detail in the subsequent specific implementation section. Description of the Drawings

[0023] The drawings are used to provide a further understanding of the present disclosure, and constitute a part of the specification. Together with the following specific implementation, they are used to explain the present disclosure, but do not constitute a limitation to the present disclosure. In the drawings:

[0024] Figure 1 It is the EBSD diagram of the metal diaphragm of the diaphragm compressor in an embodiment of the present disclosure. Specific Implementation

[0025] The following will describe in detail the specific implementation of the present disclosure with reference to the drawings. It should be understood that the specific implementation described herein is only used to illustrate and explain the present disclosure, and is not used to limit the present disclosure.

[0026] The present disclosure provides a method for preparing a metal diaphragm of a diaphragm compressor. The material of the metal diaphragm of the diaphragm compressor is GH4169, and the composition range of GH4169 is C: 0.015 - 0.06; Cr: 17 - 21; Nb: 4.75 - 5.5; Mo: 2.8 - 3.3; Al: 0.3 - 0.7; Ti: 0.75 - 1.15; Si: 0 - 0.35; Ni: the balance;

[0027] The thickness of the metal diaphragm is 0.3 - 0.8 mm;

[0028] This method includes the following steps:

[0029] S1. Place the GH4169 blank in a resistance furnace for solution treatment to obtain the material after solution treatment;

[0030] S2. Perform oil quenching treatment on the solution-treated material to obtain the material after oil quenching treatment;

[0031] S3. Perform aging treatment on the material after oil quenching treatment to obtain the metal diaphragm of the diaphragm compressor.

[0032] In the present disclosure, as Figure 1 shown, the GH4169 blank is composed of an austenite phase, a γ strengthening phase, a δ phase, and carbides. Among them, the role of the high-temperature solution treatment is to partially dissolve and transform the δ phase into the austenite phase, increase the content of the austenite phase in the metal diaphragm of the diaphragm compressor, and at the same time, the undissolved part of the δ phase plays its pinning role. Using GH4169 containing the above components in the present disclosure, within the above composition range, the mechanical properties and hydrogen embrittlement resistance of the prepared metal diaphragm of the diaphragm compressor can be ensured, meeting the requirements of the diaphragm compressor for the used metal diaphragm.

[0033] According to the present disclosure, in step S1, the solution treatment includes a heating-up treatment, and the heating rate and time of the heating-up treatment can be varied within a relatively large range. In an embodiment of the present disclosure, the heating rate of the heating-up treatment is 5°C / min - 10°C / min, and the time is 100 - 204 min.

[0034] In the present disclosure, the heating rate affects the growth of grains in the austenite phase. A fast heating rate results in a shortened growth time of the grains and smaller obtained grains. When the heating rate and time are within the ranges of the above embodiment, the growth of grains can be further ensured.

[0035] According to the present disclosure, in step S1, the solution treatment further includes an isothermal treatment, and the temperature and time of the isothermal treatment in the solution treatment can be varied within a relatively large range. In an embodiment of the present disclosure, the temperature of the isothermal treatment is 1000 - 1020°C, and the time is 1 - 2 h.

[0036] In the present disclosure, the temperature and time of the isothermal treatment play a major role in the size of grains in the austenite phase. A relatively high temperature and a relatively long treatment time of the isothermal treatment may cause the complete dissolution of the δ phase, thereby reducing its pinning effect and increasing the grain volume, affecting the mechanical properties of the formed metal diaphragm of the diaphragm compressor. A relatively low temperature of the isothermal treatment may cause the δ phase not to dissolve, resulting in a low austenite content in the metal diaphragm of the diaphragm compressor, and thus poor toughness and hydrogen embrittlement resistance of the metal diaphragm of the diaphragm compressor. Therefore, when the temperature and time of the isothermal treatment are within the above embodiment, the metal diaphragm of the diaphragm compressor after the isothermal treatment can improve the strength of the metal diaphragm of the diaphragm compressor while maintaining its relatively high toughness.

[0037] According to the present disclosure, the oil quenching treatment temperature and time can vary within a relatively wide range. In step S2, the conditions of the oil quenching treatment include: the treatment temperature is 20 - 40°C, and the time is 10 - 50 min. In the present disclosure, when the oil quenching treatment temperature and time are within the ranges of the above embodiments, the toughness of the diaphragm compressor metal diaphragm can be further increased.

[0038] According to the present disclosure, in step S3, the aging treatment includes annealing treatment, and the temperature of the annealing treatment is 700 - 750°C, and the time is 1 - 3 h.

[0039] In the present disclosure, through the annealing treatment, γ-phase is generated in the material after the oil quenching treatment, which plays a role in dispersion strengthening.

[0040] According to the present disclosure, in step S3, the aging treatment further includes tempering treatment, and the temperature of the tempering treatment is 600 - 650°C, and the time is 1 - 3 h.

[0041] In the present disclosure, after the annealing treatment, tempering treatment is carried out, which can eliminate residual stress, ensure the performance uniformity of the diaphragm compressor metal diaphragm, and also ensure that the prepared metal diaphragm has better toughness.

[0042] According to the present disclosure, the proportion of austenite phase in the diaphragm compressor metal diaphragm is 98 - 99.7%.

[0043] According to the present disclosure, the tensile strength of the diaphragm compressor metal diaphragm is 1125 - 1357 MPa.

[0044] According to the present disclosure, the elongation at break of the diaphragm compressor metal diaphragm is 25.7 - 36.3%.

[0045] According to the present disclosure, the grain size range of the diaphragm compressor metal diaphragm is 10 - 25 μm.

[0046] The present invention will be further described in detail below through examples.

[0047] Example 1

[0048] GH4169 with the composition of C: 0.06; Cr: 21; Nb: 5.5; Mo: 3.3; Al: 0.7; Ti: 1.15; Si: 0.35; Ni balance is heated at a rate of 5°C / min for 204 min to 1020°C, held at 1020°C for 1 h, the metal diaphragm after the holding treatment is subjected to oil quenching treatment for 50 min, the metal diaphragm after the oil quenching treatment is annealed at 700°C for 1 h, and then tempered at 600°C for 1 h.

[0049] Example 2

[0050] The GH4169 with the composition of C: 0.06; Cr: 21; Nb: 5.5; Mo: 3.3; Al: 0.7; Ti: 1.15; Si: 0.35; and the balance Ni is heated at a rate of 5 °C / min for 204 min to 1020 °C, held at 1020 °C for 1 h, the heat-treated metal diaphragm is subjected to oil quenching for 50 min, and the oil-quenched metal diaphragm is annealed at 750 °C for 3 h and then tempered at 650 °C for 1 h.

[0051] Example 3

[0052] The GH4169 with the composition of C: 0.06; Cr: 21; Nb: 5.5; Mo: 3.3; Al: 0.7; Ti: 1.15; Si: 0.35; and the balance Ni is heated at a rate of 10 °C / min for 100 min to 1000 °C, held at 1000 °C for 2 h, the heat-treated metal diaphragm is subjected to oil quenching for 50 min, and the oil-quenched metal diaphragm is annealed at 750 °C for 3 h and then tempered at 650 °C for 3 h.

[0053] Example 4

[0054] The same method as in Example 1 is adopted, except that it is heated at a rate of 5 °C / min for 150 min to 750 °C and held at 750 °C for 60 minutes.

[0055] Example 5

[0056] The same method as in Example 1 is adopted, except that the oil-quenched metal diaphragm is annealed at 660 °C for 1 h.

[0057] Example 6

[0058] The same method as in Example 1 is adopted, except that it is heated at a rate of 10 °C / min for 110 min to 1100 °C and held at 1100 °C for 1 h.

[0059] Comparative Example 1

[0060] The same method as in Example 1 is adopted, except that the heat-treated metal diaphragm is subjected to water quenching for 50 min.

[0061] Test Example 1

[0062] The tensile strength of the metal diaphragms prepared in Examples 1-6 and Comparative Example 1 is detected.

[0063] The tensile strength test was carried out on a universal material testing machine according to "GB / T 228.1-2010 Metallic materials - Tensile testing - Part 1: Method of test at room temperature".

[0064] Test Example 2

[0065] The elongation at break of the metal diaphragms prepared in Examples 1-6 and Comparative Example 1 was detected.

[0066] The elongation at break test was carried out on a universal material testing machine according to "GB / T 228.1-2010 Metallic materials - Tensile testing - Part 1: Method of test at room temperature".

[0067] Test Example 3

[0068] The average grain size of the metal diaphragms prepared in Examples 1-6 and Comparative Example 1 was detected.

[0069] The microstructure of the samples was observed by scanning electron microscopy and the average grain size was measured by electron backscatter diffraction according to "GB / T36165-2018 Metallic materials - Determination of average grain size".

[0070] Test Example 4

[0071] The austenite phase of the metal diaphragms prepared in Examples 1-6 and Comparative Example 1 was detected.

[0072] The austenite content was measured by X-ray diffractometer according to "YB / T5338-2019 Steel - Quantitative determination of austenite - X-ray diffractometer method".

[0073] The test results are shown in Table 1.

[0074] Table 1

[0075]

[0076] As can be seen from Table 1, the diaphragm compressor metal diaphragm prepared by the method of the present disclosure has the advantages of high tensile strength, good toughness, uniform grain size, small distribution range and high austenite content.

[0077] By comparing Example 1 with Comparative Example 1, it can be seen that for the water quenching treatment used in Comparative Example 1, the austenite content, elongation at break, average grain size and tensile strength of the diaphragm compressor metal diaphragm obtained are lower than those of Example 1, indicating that the oil quenching treatment used in Example 1 is more conducive to preparing a diaphragm compressor metal diaphragm with high tensile strength, good toughness, uniform grain size and high austenite content.

[0078] As can be seen from the comparison between Example 1 and Examples 4 and 6, the diaphragm compressor metal diaphragm obtained by subjecting Example 1 to isothermal treatment at the isothermal treatment temperature provided by the present disclosure has a high austenite content, good toughness, and good tensile strength.

[0079] As can be seen from the comparison between Example 1 and Example 5, the diaphragm compressor metal diaphragm obtained by subjecting Example 1 to annealing treatment at the annealing treatment temperature provided by the present disclosure has a high austenite content, good toughness, and good tensile strength.

[0080] The preferred embodiments of the present disclosure have been described in detail above. However, the present disclosure is not limited to the specific details in the above embodiments. Within the scope of the technical concept of the present disclosure, various simple modifications can be made to the technical solutions of the present disclosure, and these simple modifications all fall within the protection scope of the present disclosure.

[0081] In addition, it should be noted that, among the various specific technical features described in the above specific embodiments, they can be combined in any appropriate manner without conflict. To avoid unnecessary repetition, the present disclosure will not separately describe various possible combination methods.

[0082] In addition, any combination can be made between various different embodiments of the present disclosure, as long as it does not violate the idea of the present disclosure, it should also be regarded as the content disclosed by the present disclosure.

Claims

1. A preparation method of a metal diaphragm for a diaphragm compressor, characterized in that, The material of the metal diaphragm of the diaphragm compressor is GH4169, and the composition range of GH4169 is C: 0.015 - 0.06; Cr: 17 - 21; Nb: 4.75 - 5.5; Mo: 2.8 - 3.3; Al: 0.3 - 0.7; Ti: 0.75 - 1.15; Si: 0 - 0.35; Ni: the balance; The thickness of the metal diaphragm is 0.3 - 0.8 mm; The method comprises the following steps: S1. Place the GH4169 blank in a resistance furnace for solution treatment to obtain the material after solution treatment; S2. Perform oil quenching treatment on the material after solution treatment to obtain the material after oil quenching treatment; S3. Perform aging treatment on the material after oil quenching treatment to obtain the metal diaphragm of the diaphragm compressor.

2. The method according to claim 1, wherein, In step S1, the solution treatment includes heating treatment, and the heating rate of the heating treatment is 5 °C / min - 10 °C / min, and the time is 100 - 204 min.

3. The method according to claim 1, wherein, In step S1, the solution treatment further includes constant temperature treatment, and the temperature of the constant temperature treatment is 1000 - 1020 °C, and the time is 1 - 2 h.

4. The method according to claim 1, wherein In step S2, the conditions of the oil quenching treatment include: the treatment temperature is 20 - 40 °C, and the time is 10 - 50 min.

5. The method according to claim 1, wherein, In step S3, the aging treatment includes annealing treatment, and the temperature of the annealing treatment is 700 - 750 °C, and the time is 1 - 3 h.

6. The method according to claim 1, wherein In step S3, the aging treatment further includes tempering treatment, and the temperature of the tempering treatment is 600 - 650 °C, and the time is 1 - 3 h.

7. The method according to claim 1, wherein The proportion of the austenite phase in the metal diaphragm of the diaphragm compressor is 98 - 99.7%.

8. The method according to claim 1, wherein The tensile strength of the metal diaphragm of the diaphragm compressor is 1125 - 1357 MPa.

9. The method according to claim 1, wherein The elongation at break of the metal diaphragm of the diaphragm compressor is 25.7 - 36.3%.

10. The method according to claim 1, wherein, The grain size range of the metal diaphragm of the diaphragm compressor is 10 - 25 μm.

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