Corrosion-resistant, wear-resistant and high-temperature-resistant Fe-Cr-Mo-C-B amorphous alloy and high-throughput screening method and application thereof

Abstract

The invention discloses a corrosion-resistant, wear-resistant and high-temperature-resistant Fe-Cr-Mo-C-B amorphous alloy as well as a high-throughput screening method and application thereof, and the component expression of the alloy is FeaCrbMocCdBe, 17 lt, a < lt >; 55, 12 lt; blt; 49, 9lt; clt; ct; 18, 12 lt; dlt; 16, 8lt; lt, lt; 11. The screening method comprises the following steps: providing a target material, wherein components of the target material are selected according to composition requirements of a target alloy; a target material is installed, and Fe-Cr-Mo-C-B alloy is deposited on a substrate material through a co-sputtering method; the electrochemical performance of the sample is measured, and alloy components with excellent corrosion resistance are screened out through test data. According to the method, simultaneous deposition of different alloy components is achieved in a single experiment, the preparation efficiency is greatly improved, the alloy components with excellent corrosion resistance are screened out by conducting systematic measurement on the corrosion resistance of alloy films with different components, and the prepared coating is resistant to corrosion, abrasion and high temperature corrosion.

Description

Technical Field

[0001] The invention relates to an Fe-based amorphous alloy and a preparation method and application thereof, and in particular to a corrosion-resistant, wear-resistant and high-temperature-resistant Fe-Cr-Mo-CB amorphous alloy and a high-throughput screening method and application thereof. Background Art

[0002] The corrosion problem of materials is particularly severe in the fields of marine engineering, petrochemicals, nuclear power and ships, especially stress corrosion, pitting corrosion and general corrosion. Factors such as high salt spray, scouring and biofouling in the marine environment make marine equipment and projects prone to corrosion damage, wear failure and biofouling during long-term service, seriously affecting their reliability and service life, and further affecting the reliability and service life of marine equipment. Therefore, it is particularly important to develop materials with excellent corrosion and wear resistance for equipment serving in the marine environment.

[0003] Amorphous alloys exhibit excellent corrosion resistance and wear resistance due to their lack of long-range ordered atomic structure and lack of crystal defects. Among various amorphous alloys, iron-based amorphous alloys have attracted widespread attention due to their high strength, excellent corrosion resistance and low cost. However, for multi-component alloys, their composition regulation is complex, the research and development cost is high, and the cycle is long, which makes traditional methods face huge challenges in exploring and discovering high-performance amorphous alloys. Therefore, in order to improve the efficiency of screening and development of corrosion-resistant materials and ultimately achieve the goal of "design on demand", it is particularly important to develop efficient material corrosion behavior screening technology.

[0004] High-throughput screening technology for amorphous alloys can accelerate the discovery and optimization of new materials, especially in terms of corrosion resistance and mechanical properties. Techniques such as mechanical alloying and solution deposition can quickly prepare amorphous alloy films or micro-alloy samples, allowing researchers to synthesize a large number of alloys with different compositions in a short period of time, providing an experimental basis for high-throughput screening. However, there is currently no high-throughput screening method for iron-based amorphous alloys that can systematically optimize their corrosion resistance, wear resistance and high-temperature stability. Summary of the invention

[0005] Purpose of the invention: The purpose of the present invention is to provide a Fe-Cr-Mo-CB amorphous alloy which is corrosion-resistant, wear-resistant and high temperature-resistant;

[0006] The second object of the present invention is to provide a high-throughput screening method for quickly and efficiently screening Fe-Cr-Mo-CB amorphous alloys with excellent corrosion resistance;

[0007] The third object of the present invention is to provide an application of a Fe-Cr-Mo-CB amorphous alloy that is corrosion-resistant, wear-resistant and high-temperature-resistant.

[0008] Technical solution: The corrosion-resistant, wear-resistant and high-temperature-resistant Fe-Cr-Mo-CB amorphous alloy of the present invention has a composition expression of: Fe a Cr b Mo c C d B e , of which 17 <a<55,12<b<49,9<c<18,12<d<16,8<e<11。

[0009] In the alloy prepared by magnetron co-sputtering, the content of each metal element changes in a gradient along the direction away from the target material; while the content of non-metallic elements does not change significantly along the direction away from the target material.

[0010] Among them, the composition gradient of Fe is 17-55at.%, the composition gradient of Cr is 12-49at.%, the composition gradient of Mo is 9-18at.%, the composition gradient of C is 12-16at.%, and the composition gradient of B is 8-11at.%.

[0011] Wherein, the Fe—Cr—Mo—CB amorphous alloy is one of an amorphous alloy film, an amorphous alloy strip or an amorphous alloy coating.

[0012] The high-throughput screening method for the corrosion-resistant, wear-resistant and high-temperature-resistant Fe-Cr-Mo-CB amorphous alloy comprises the following steps:

[0013] (1) Providing the required target material, the composition of the target material is selected according to the composition requirements of the target alloy;

[0014] (2) installing a target material and depositing a Fe-Cr-Mo-CB amorphous alloy sample on a substrate material by magnetron co-sputtering;

[0015] (3) Measuring the electrochemical properties of the sample obtained in step (2), and screening out alloy components with excellent corrosion resistance through the test data.

[0016] The "high throughput" mentioned in the present invention refers to obtaining a large number of alloy samples by co-sputtering at one time.

[0017] Wherein, in step (1), the target material selected is a powder sintered alloy target; the composition of the alloy target material selected includes Fe 100-2x C x B x ,Cr 100-2x C x B x and Mo 100-2x C x B x , of which 5 <x<15。

[0018] Wherein, in step (2), the Fe 100-2x C x B x Alloy target sputtering power is 90-140W, Cr 100-2x C x B x Alloy target sputtering power is 70-120W, Mo 100-2x C x B x The alloy target sputtering power is 40-60W.

[0019] Wherein, in step (2), Fe 100-2x C x B x Alloy target and Cr 100-2x C x B x The alloy target is placed at an angle when installed, preferably at an angle of 30°. 100-2x C x B x The alloy targets are placed in parallel.

[0020] In the step (3), the thin film samples for electrochemical measurement are first polished on all sides with 1000-mesh sandpaper to ensure the accuracy and reliability of the electrochemical test results.

[0021] Among them, in step (3), the electrochemical test includes self-corrosion potential, self-corrosion current density measurement and corrosion resistance evaluation, and the alloy components with excellent corrosion resistance are screened out through these test data.

[0022] The above-mentioned corrosion-resistant, wear-resistant and high-temperature resistant Fe-Cr-Mo-CB amorphous alloy is used in the preparation of a coating. The Fe-Cr-Mo-CB amorphous alloy coating has the alloy composition as mentioned above. When preparing the Fe-Cr-Mo-CB amorphous alloy coating, the fuel flow rate is set to 6.0-6.5GPH.

[0023] The specific preparation process is as follows: (1) preparing a master alloy by vacuum induction melting according to the required composition, then crushing the master alloy and placing it in a gas atomization powder making furnace, and obtaining amorphous powder by gas atomization under the protection of argon gas, and selecting powder with a particle size of less than 50 μm as the raw material for thermal spray coating;

[0024] (2) Using supersonic flame spraying, the amorphous powder prepared in step (1) is used to prepare a coating on the surface of the substrate, and the process parameters are: fuel flow rate 6.0-6.5 GPH.

[0025] Among them, other flow parameters in step (2) are: oxygen flow rate 1850SCFH, carrier gas rate 12L / min, powder delivery rate 60g / min, and spraying distance 270mm.

[0026] Beneficial effects: Compared with the prior art, the present invention achieves the following significant effects:

[0027] (1) Compared with other alloy components, the increase in the content of Cr, which has a higher melting point and is more easily passivated, will improve its corrosion resistance and high-temperature stability, and the appearance of the crystallized phase in the coating will improve its wear resistance to a certain extent. The corrosion resistance and wear resistance are mainly due to the increase in the Cr content and the decrease in the Fe content. The Mo element can promote amorphous formation and high-temperature stability, and C and B can promote amorphous formation and wear resistance. The Fe-Cr-Mo-CB amorphous alloy developed by the present invention has excellent corrosion resistance, wear resistance and high-temperature stability.

[0028] (2) The preparation method of the present invention can prepare a large amount of Fe-Cr-Mo-CB alloys with a composition gradient distribution through a single co-sputtering. This method realizes the simultaneous deposition of different alloy components in a single experiment, greatly improving the preparation efficiency. By systematically measuring the corrosion resistance of alloy films with different components, alloy components with excellent corrosion resistance are screened out.

[0029] (3) Compared with the traditional method, the high-throughput screening method for corrosion resistance proposed in the present invention has significant advantages. Its operation process is simple and convenient, and does not require complicated alloy target material replacement or tedious steps. It can efficiently prepare Fe-Cr-Mo-CB alloy films with various compositions.

[0030] (4) The method of the present invention not only reduces the time and cost of the experiment, but also can quickly screen out the best corrosion-resistant alloy in a wide range of composition spaces, providing an efficient and low-cost technical means for the development of high-performance corrosion-resistant materials.

[0031] (5) The method of the present invention also has good scalability and can be applied to high-throughput screening of different types of amorphous alloy systems, providing strong support for the design and development of future corrosion-resistant materials. BRIEF DESCRIPTION OF THE DRAWINGS

[0032] Figure 1 Schematic diagram of the magnetron co-sputtering system in Example 1 of the present invention used to prepare a Fe-Cr-Mo-CB material library;

[0033] Figure 2 is a graph showing the variation of film thickness of the Fe-Cr-Mo-CB material library prepared in Example 2 of the present invention with the sputtering time;

[0034] Figure 3 is an X-ray diffraction pattern of the Fe-Cr-Mo-CB material library prepared in Example 3 of the present invention;

[0035] Figure 4 is a scanning electron microscope image of the Fe-Cr-Mo-CB material library prepared in Example 3 of the present invention;

[0036] Figure 5 TEM image of the Fe-Cr-Mo-CB material library prepared in Example 3 of the present invention;

[0037] Figure 6 : is a distribution diagram of various element components of the Fe-Cr-Mo-CB material library prepared in Example 3 of the present invention;

[0038] Figure 7 is a graph showing changes in the self-corrosion potential, self-corrosion current density and passivation current density of the Fe-Cr-Mo-CB material library prepared in Example 3 of the present invention;

[0039] Figure 8 The X-ray diffraction pattern and differential scanning calorimetry pattern of the Fe-Cr-Mo-CB strips prepared in Examples 4-8 of the present invention;

[0040] Fig. 9 The potentiodynamic polarization curves and AC impedance diagrams of the Fe-Cr-Mo-CB strips prepared in Examples 4-8 of the present invention;

[0041] Fig.10 X-ray diffraction diagram, potentiodynamic polarization curve diagram, friction coefficient diagram and wear rate diagram of the amorphous powder and Fe-Cr-Mo-CB coating prepared in Example 9 of the present invention;

[0042] Fig.11 XRD diagrams of the amorphous powder of Example 9 and the coatings of Examples 9-11 of the present invention;

[0043] Fig.12 The DSC graphs of the amorphous powder of Example 9 and the coatings of Examples 9-11 of the present invention;

[0044] Fig.13 This is a physical comparison diagram of the high temperature corrosion resistance of Q235 steel and the coating of Example 9 of the present invention;

[0045] Fig.14 Shown are the hardness test results of the amorphous powder of Example 9 and the coatings of Examples 9-11. DETAILED DESCRIPTION

[0046] The present invention is described in further detail below.

[0047] Example 1

[0048] A corrosion-resistant, wear-resistant and high-temperature-resistant Fe-Cr-Mo-CB amorphous alloy film, and a high-throughput screening method thereof, such as Figure 1 As shown, the following steps are included:

[0049] (1) Preparation of Fe by powder hot pressing sintering 80 C 10 B 10 Cr 80 C 10 B 10 and Mo 80 C 10 B 10 Alloy target, with a target diameter of 60mm and a thickness of 3mm, ensures the uniformity and high density of the alloy target, which is suitable for subsequent sputtering deposition process;

[0050] (2) Fe 80 C 10 B 10 Alloy target, Cr 80 C 10 B 10 Alloy target and Mo 80 C 10 B 10 The alloy target is installed in the magnetron sputtering equipment, Fe 80 C 10 B 10 Alloy target and Cr 80 C 10 B 10 The target tilt angle of the alloy target was set to 30°, and the Mo 80 C 10 B 10 The alloy targets are placed in parallel to ensure uniform sputtering of each element during the sputtering process and achieve the expected composition gradient;

[0051] (3) 69 8×8×0.5 mm single crystal silicon wafers were glued to the sample platform with conductive adhesive to ensure good electrical connection between the sample and the platform; then, the sample platform was placed above the target material, with the specific position relationship as shown in the figure. Figure 1 As shown; by optimizing the relative position between the sample stage and the target material, it is ensured that a film with a composition gradient distribution is obtained at different positions;

[0052] (4)Fe 80 C 10 B 10 The alloy target is connected to a DC power supply, Cr 80 C 10 B 10 The alloy target is connected to a DC pulse power supply, Mo 80 C 10B 10 The alloy target was connected to a DC pulse power supply, the power values ​​of each target were shown in Table 1, and the sputtering time was 2 hours.

[0053] Table 1 shows the relationship between the composition distribution of the Fe-Cr-Mo-CB material library and the target power. The results show that the composition gradient of each metal element in the material library is large, including most of the components in the system. The X-ray diffraction patterns of all thin film alloys in this embodiment also show a completely amorphous structure.

[0054] Table 1

[0055]

[0056] Example 2

[0057] A corrosion-resistant, wear-resistant and high-temperature-resistant Fe-Cr-Mo-CB amorphous alloy film, and a high-throughput screening method thereof, comprising the following steps:

[0058] (1) Preparation of Fe by powder hot pressing sintering 80 C 10 B 10 Cr 80 C 10 B 10 and Mo 80 C 10 B 10 Alloy target, with a target diameter of 60mm and a thickness of 3mm, ensures the uniformity and high density of the alloy target, which is suitable for subsequent sputtering deposition process;

[0059] (2) Fe 80 C 10 B 10 Alloy target, Cr 80 C 10 B 10 Alloy target and Mo 80 C 10 B 10 The alloy target is installed in the magnetron sputtering equipment, Fe 80 C 10 B 10 Alloy target and Cr 80 C 10 B 10 The target tilt angle of the alloy target was set to 30°, and the Mo 80 C 10 B 10 The alloy targets are placed in parallel to ensure uniform sputtering of each element during the sputtering process and achieve the expected composition gradient.

[0060] (3) Glue 69 8×8×0.5 mm single crystal silicon wafers onto the sample platform with conductive adhesive to ensure good electrical connection between the sample and the platform. Then, place the sample platform above the target. The specific position relationship is as follows: Figure 1 As shown; by optimizing the relative position between the sample stage and the target material, it is ensured that a film with a composition gradient distribution is obtained at different positions;

[0061] (4)Fe 80 C 10 B 10 The alloy target was connected to a DC power supply, and the sputtering power was set to 130 W. 80 C 10 B 10 The alloy target is connected to a DC pulse power supply, the sputtering power is 110W, and the Mo 80 C 10 B 10 The alloy target was connected to a DC pulse power supply, and the sputtering power was 50 W; the sputtering time was set to 0 min, 30 min, 60 min, 90 min, 120 min, and 150 min.

[0062] Figure 2 This is a graph showing the variation of film thickness of the Fe-Cr-Mo-CB material library with sputtering time. The inset is the corresponding actual sample picture. The results show that the thickness of the sample is proportional to the sputtering time, but as the sputtering time increases to 150 minutes, the film surface curls and falls off.

[0063] The X-ray diffraction patterns of all the thin film alloys in this embodiment also show a completely amorphous structure.

[0064] Example 3

[0065] A corrosion-resistant, wear-resistant and high-temperature-resistant Fe-Cr-Mo-CB amorphous alloy film, and a high-throughput screening method thereof, the specific steps are as follows:

[0066] (1) Preparation of Fe by powder hot pressing sintering 80 C 10 B 10 Cr 80 C 10 B 10 and Mo 80 C 10 B 10 Alloy target, with a target diameter of 60mm and a thickness of 3mm, ensures the uniformity and high density of the alloy target, which is suitable for subsequent sputtering deposition process;

[0067] (2) Fe 80 C 10 B 10 Alloy target, Cr 80 C10 B 10 Alloy target and Mo 80 C 10 B 10 The alloy target is installed in the magnetron sputtering equipment, Fe 80 C 10 B 10 Alloy target and Cr 80 C 10 B 10 The target tilt angle of the alloy target was set to 30°, and the Mo 80 C 10 B 10 The alloy targets are placed in parallel to ensure uniform sputtering of each element during the sputtering process and achieve the expected composition gradient;

[0068] (3) 69 8×8×0.5 mm single crystal silicon wafers were glued to the sample platform with conductive adhesive to ensure good electrical connection between the sample and the platform; then, the sample platform was placed above the target material, with the specific position relationship as shown in the figure. Figure 1 As shown; by optimizing the relative position between the sample stage and the target material, it is ensured that a film with a composition gradient distribution is obtained at different positions;

[0069] (4)Fe 80 C 10 B 10 The alloy target was connected to a DC power supply, and the sputtering power was set to 130 W. 80 C 10 B 10 The alloy target is connected to a DC pulse power supply, the sputtering power is 110W, and the Mo 80 C 10 B 10 The alloy target was connected to a DC pulse power supply, the sputtering power was 50 W, and the sputtering time was 120 min.

[0070] Figure 3 The X-ray diffraction pattern of the prepared Fe-Cr-Mo-CB alloy film is shown in Figure 1. The results show that all the thin film alloys present a broad diffuse diffraction peak, indicating that the film has an amorphous structure.

[0071] Figure 4 The SEM image of the prepared Fe-Cr-Mo-CB alloy film is shown. It can be observed that the film has a thickness of about 1.5 μm and a smooth surface without obvious cracks or voids, showing good structural integrity.

[0072] Figure 5The figure shows the TEM image of the prepared Fe-Cr-Mo-CB alloy film. It can be seen that too high Cr content will cause the Cr element to exceed the solid solubility of the alloy itself, precipitate next to it, and form Cr-poor and Cr-rich areas. The alloy is more susceptible to galvanic corrosion and its corrosion resistance is reduced.

[0073] Figure 6 The figure shows the distribution of various element compositions of the prepared Fe-Cr-Mo-CB alloy film. It can be seen that this range covers most of the iron-based amorphous alloy coating compositions. Figure 6 The metal content decreases as the distance between the sample and the target increases, as shown in the contours in (b)-(f). Since the concentrations of C and B are the same on each target, the metalloid content of the sample changes only slightly.

[0074] Figure 7 The electrochemical performance analysis results of the prepared Fe-Cr-Mo-CB alloy film in 3.5wt.% NaCl solution, including the relationship between the self-corrosion potential, self-corrosion current density and passivation current density as a function of the metal elements. The test results show that the concentrations of Fe and Cr have a significant effect on the corrosion resistance of the alloy, while the effect of Mo is relatively small. In particular, when the composition gradient of the metal element Fe is 24-34at.% and the composition gradient of Cr is 30-40at.%, the alloy film exhibits excellent stability and corrosion resistance in a corrosive environment.

[0075] Example 4

[0076] Corrosion-resistant, wear-resistant and high-temperature resistant alloy strip, the specific composition is Fe 19 Cr 44 Mo 12 C 15 B 10 , recorded as Cr44-ribbon, and its preparation method comprises the following steps:

[0077] Fe-Cr-Mo-CB alloy ingots were prepared by induction melting, and then the master alloy was crushed and put into a belt-spinning furnace to obtain amorphous strips under the protection of argon.

[0078] Example 5

[0079] Based on Example 4, the difference from Example 4 is that the composition of the alloy strip is Fe 24 Cr 39 Mo 14 C 14 B 9 , recorded as Cr39-ribbon.

[0080] Example 6

[0081] Based on Example 4, the difference from Example 4 is that the composition of the alloy strip is Fe 31 Cr 31 Mo 14 C 14 B 10 , recorded as Cr31-ribbon.

[0082] Example 7

[0083] Based on Example 4, the difference from Example 4 is that the composition of the alloy strip is Fe 41 Cr 21 Mo 14 C 15 B 9 , recorded as Cr21-ribbon.

[0084] Example 8

[0085] Based on Example 4, the difference from Example 4 is that the composition of the alloy strip is Fe 55 Cr 12 Mo 10 C 14 B 9 , recorded as Cr12-ribbon.

[0086] The following tests were performed on Examples 4-8:

[0087] like Figure 8 As shown, Figure 8 (a) is the X-ray diffraction pattern of the Fe-Cr-Mo-CB alloy strips obtained in Examples 4 to 8. The results show that all the alloy strips present a broad diffuse diffraction peak, indicating that they are amorphous structures.

[0088] Figure 8 (b) is a differential scanning calorimetry diagram of the Fe-Cr-Mo-CB alloy strip obtained in Examples 4 to 8. The results show that the Cr31-ribbon, Cr39-ribbon and Cr44-ribbon alloys have higher glass transition temperatures and higher crystallization temperatures, indicating that the alloys have excellent high temperature stability.

[0089] Fig. 9Potentiodynamic polarization curves and AC impedance diagrams of Fe-Cr-Mo-CB alloy strips in 3.5wt.% NaCl solution were obtained for Examples 4-8. As can be seen from the figure, Cr31-ribbon and Cr39-ribbon both exhibited a wider passivation range, lower passivation current density, lower passivation current density and higher corrosion potential in 3.5wt.% NaCl solution. The results show that Cr31-ribbon and Cr39-ribbon alloys exhibit excellent stability and corrosion resistance in a corrosive environment.

[0090] Example 9

[0091] A corrosion-resistant, wear-resistant and high-temperature-resistant Fe-Cr-Mo-CB amorphous alloy coating, the composition of which is Fe 31 Cr 31 Mo 14 C 14 B 10 , and its preparation method comprises the following steps:

[0092] (1) preparing a master alloy by vacuum induction melting according to the required composition, then crushing the master alloy and placing it in a gas atomization powder making furnace, and obtaining amorphous powder by gas atomization under the protection of argon gas, and selecting powder with a particle size of less than 50 μm as the raw material for thermal spray coating;

[0093] (2) Using the supersonic flame spraying method, the amorphous powder prepared in step (1) is used to prepare a coating on the surface of a 304 stainless steel substrate. The process parameters are: oxygen flow rate 1850 SCFH, fuel flow rate 6.2 GPH, carrier gas rate 12 L / min, powder feeding rate 60 g / min, and spraying distance 270 mm.

[0094] Fig.10 (a) is the X-ray diffraction pattern of the amorphous powder and coating obtained in Example 9. The results show that both the powder and the coating have crystallization peaks.

[0095] Fig.10 (b) is the potentiodynamic polarization curve of the amorphous coating and 304SS prepared in Example 9 in 3.5wt.% NaCl solution. It can be seen from the figure that the prepared amorphous coating exhibits a wide passivation range, a lower passivation current density, a lower passivation current density and a higher corrosion potential in 3.5wt.% NaCl solution; the corrosion resistance of the prepared amorphous coating is much better than that of 304SS.

[0096] Fig.10 (c) is the friction coefficient curve of the amorphous coating and 304SS prepared in Example 9. The results show that the friction coefficient of the coating is stable and its wear rate is 0.6×10 -6 mm3 N -1 m -1 Much lower than the wear rate of the substrate, such as Fig.10 (d) in.

[0097] Example 10

[0098] Based on Example 9, the difference from Example 9 is that the fuel flow rate is 6.0 GPH.

[0099] Embodiment 11

[0100] Based on Example 9, the difference from Example 9 is that the fuel flow rate is 6.5 GPH.

[0101] like Fig.11 Shown are the XRD patterns of the amorphous powder of Example 9 and the coatings of Examples 9-11. It can be seen that both the powder and the coatings have crystallization peaks. Fig.11 SV6.0, SV6.2, and SV6.5 refer to coating samples with fuel flow rates of 6.0, 6.2, and 6.5, respectively, the same below.

[0102] like Fig.12 The DSC test diagrams of the amorphous powder of Example 9 and the coatings of Examples 9-11 are shown. It can be seen that the Tg and Tx of each coating are slightly lower than those of the powder, but there is no obvious difference, and the Tg and Tx of the coatings with three different heat inputs, i.e., three different fuel flow rates, are almost unchanged, and the effect of heat input on the thermodynamic properties of the coatings can be ignored. The Tg of the coatings of Examples 9-11 is as high as 666°C, indicating that the three coatings have excellent high temperature stability.

[0103] The B element content in the system of the present invention is relatively high, reaching 10 atomic ratios, which greatly improves the resistance to high temperature corrosion and neutron radiation.

[0104] Fig.13 The figure is a comparison of the high temperature corrosion resistance of Q235 steel and the coating of Example 9 of the present invention. The left figure is a physical picture of Q235 steel corroded at 600°C for 24h, and the right figure is a physical picture of the coating of Example 9 corroded at 600°C for 96h. The corrosion environment is: 2-3 mg of NaCl: Na 2 SO 4 =1:3 mixed salt, replenish salt every 24 hours.

[0105] like Fig.14The hardness test results of the amorphous powder of Example 9 and the coatings of Examples 9-11 under different microhardness load conditions of 0.3kg, 0.5kg, and 1kg are shown. It can be seen that all coatings have high hardness, which is due to the presence of the crystallized phase inside the coating. When the crystallized phase is evenly distributed in the amorphous matrix, a dispersion strengthening effect will be generated, thereby improving the overall hardness of the material.

[0106] Comparative Example 1

[0107] (1) Preparation of Cr by powder hot pressing sintering 2 Mo alloy target, Fe target and graphite target, the target diameter is 60mm and the thickness is 3mm;

[0108] (2) Fe target, Cr 2 Mo alloy target and graphite target are installed in the magnetron sputtering equipment, Fe target and Cr 2 The target inclination angle of the Mo alloy target was set to 30°, and the graphite target was placed in parallel to ensure uniform sputtering of each element during the sputtering process and achieve the expected composition gradient;

[0109] (3) 69 8×8×0.5 mm single crystal silicon wafers were glued to the sample platform with conductive adhesive to ensure good electrical connection between the sample and the platform. Subsequently, the sample platform was placed on the target material, and the relative position between the sample platform and the target material was optimized to ensure that a film with a composition gradient distribution was obtained at different positions;

[0110] (4)Fe 80 C 10 B 10 The alloy target is connected to a DC power supply, Cr 80 C 10 B 10 The alloy target is connected to a DC pulse power supply, Mo 80 C 10 B 10 The alloy target was connected to a DC pulse power supply, and the sputtering time was 2 hours.

[0111] Table 2 shows the relationship between the composition distribution of the Fe-Cr-Mo-C material library and the power of each target. The results show that no matter how the power of each target is adjusted, it is difficult to achieve a large range of changes in each metal element, mainly because the Cr element and the Mo element are in one target, and the Mo element content is small and the atomic mass is heavy. The X-ray diffraction patterns of all thin film alloys in this comparative example show a completely amorphous structure.

[0112] Table 2

[0113]

Claims

1. A corrosion-resistant, wear-resistant and high-temperature-resistant Fe-Cr-Mo-CB amorphous alloy, characterized in that: The composition expression of the Fe-Cr-Mo-CB amorphous alloy is: Fe a Cr b Mo c C d B e , of which 17 <a<55,12<b<49,9<c<18,12<d<16,8<e<11。 2. The corrosion-resistant, wear-resistant and high-temperature-resistant Fe-Cr-Mo-CB amorphous alloy according to claim 1, characterized in that: In the process of preparing the Fe-Cr-Mo-CB amorphous alloy by magnetron co-sputtering, the content of each metal element changes gradually in the direction away from the target material.

3. The corrosion-resistant, wear-resistant and high-temperature-resistant Fe-Cr-Mo-CB amorphous alloy according to claim 2, characterized in that: The composition gradient of Fe is 17-55 at.%, the composition gradient of Cr is 12-49 at.%, the composition gradient of Mo is 9-18 at.%, the composition gradient of C is 12-16 at.%, and the composition gradient of B is 8-11 at.%.

4. The corrosion-resistant, wear-resistant and high-temperature-resistant Fe-Cr-Mo-CB amorphous alloy according to claim 1, characterized in that: The Fe—Cr—Mo—CB amorphous alloy is one of an amorphous alloy film, an amorphous alloy strip or an amorphous alloy coating.

5. A high-throughput screening method for corrosion-resistant, wear-resistant and high-temperature-resistant Fe-Cr-Mo-CB amorphous alloy according to claim 1, characterized in that: The following steps are involved: (1) Providing the required target material, the composition of the target material is selected according to the composition requirements of the target alloy; (2) installing a target material and depositing a Fe-Cr-Mo-CB amorphous alloy sample on a substrate material by magnetron co-sputtering; (3) Conducting electrochemical property measurements on the samples obtained in step (2), and screening out alloy components with excellent corrosion resistance based on the test data.

6. The high-throughput screening method for corrosion-resistant, wear-resistant and high-temperature-resistant Fe-Cr-Mo-CB amorphous alloy according to claim 5, characterized in that: In step (1), the target material selected is a powder sintered alloy target.

7. The high-throughput screening method for corrosion-resistant, wear-resistant and high-temperature-resistant Fe-Cr-Mo-CB amorphous alloy according to claim 5, characterized in that: In step (1), the composition of the alloy target selected includes Fe 100-2x C x B x ,Cr 100-2x C x B x and Mo 100- 2x C x B x , of which 5 <x<15。 8. The high-throughput screening method for corrosion-resistant, wear-resistant and high-temperature-resistant Fe-Cr-Mo-CB amorphous alloy according to claim 5, characterized in that: In step (2), the Fe 100-2x C x B x Alloy target sputtering power is 90-140W, Cr 100-2x C x B x Alloy target sputtering power is 70-120W, Mo 100-2x C x B x The alloy target sputtering power is 40-60W.

9. The high-throughput screening method for corrosion-resistant, wear-resistant and high-temperature-resistant Fe-Cr-Mo-CB amorphous alloy according to claim 5, characterized in that: In step (2), Fe 100-2x C x B x Alloy target and Cr 100-2x C x B x The alloy target is placed tilted when the target is installed. 100-2x C x B x The alloy targets are placed in parallel.

10. Application of a corrosion-resistant, wear-resistant and high-temperature-resistant Fe-Cr-Mo-CB amorphous alloy in the preparation of a coating, characterized in that: The Fe-Cr-Mo-CB amorphous alloy coating has the alloy composition as claimed in claim 1. When preparing the Fe-Cr-Mo-CB amorphous alloy coating, the fuel flow rate is set to 6.0-6.5 GPH.

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