Glass manufacturing components and methods for manufacturing the same

Abstract

In glass manufacturing components having a coating formed from a Ni-based self-fluxing alloy, the wear resistance of the coating is improved. [Solution] A glass manufacturing component 1 for transporting or shaping glass with a viscosity logη = 3 to 14.6 has a main body 11 made of metal and a coating 12 formed on the surface of the main body by a Ni-based self-fluxing alloy. The Ni-based self-fluxing alloy contains P greater than 0 mass% and less than or equal to 3 mass%, Si greater than 0 mass% and less than or equal to 5 mass%, and residual Ni in a larger amount than other components. The metal structure of the coating includes a first phase and a second phase. The concentration of P in the first phase is higher than the average concentration of P in the entire Ni-based self-fluxing alloy, and the concentration of P in the second phase is lower than the concentration of P in the first phase. In an image of the metal structure observed under a microscope, the area ratio of the second phase in a 10 μm square area is in the range of 0 to 0.7.

Description

Technical Field

[0001] The present invention relates to a member for glass production and a method for manufacturing the same.

Background Art

[0002] In the glass product forming process, if the member for glass production easily adheres to the glass in a high-temperature state, molding defects such as inability to accurately shape the product during molding or damage to the surface of the glass product may occur. Therefore, for example, in the molding of glass bottles, a mold release agent is frequently applied (referred to as swabbing) to ensure mold release. Hereinafter, in the text, glass in a high-temperature state that can be subjected to molding processing, that is, glass having a viscosity of logη = 3 to 14.6 (= 10 3 ~10 14.6 poise) and its mass are defined as "molten glass" or "molten glass mass". Here, logη is the common logarithm.

[0003] Patent Document 1 discloses a Ni-based self-fluxing alloy used as a coating for a member for glass production. The Ni-based self-fluxing alloy contains B (boron) and Si (silicon). The Ni-based self-fluxing alloy may contain P (phosphorus). This Ni-based self-fluxing alloy has the characteristic of low adhesiveness to molten glass.

Prior Art Documents

Patent Documents

[0004]

Patent Document 1

Summary of the Invention

Problems to be Solved by the Invention

[0005] The inventors of this invention have confirmed that coatings formed from Ni-based self-fluxing alloys exhibit reduced wear resistance when P is present compared to coatings without P. Therefore, there is a need to improve the wear resistance of coatings formed from Ni-based self-fluxing alloys containing P.

[0006] In view of the above background, the present invention aims to improve the wear resistance of a coating formed from a Ni-based self-fluxing alloy in a glass manufacturing component. Furthermore, it aims to provide a method for manufacturing a glass manufacturing component having a coating with high wear resistance. [Means for solving the problem]

[0007] One aspect of the present invention is a glass manufacturing member (1) for conveying or shaping glass having a viscosity logη = 3 to 14.6, comprising a body (11) made of metal and a coating (12) formed on the surface of the body by a Ni-based self-fluxing alloy, wherein the Ni-based self-fluxing alloy contains P greater than 0 mass% and 3 mass% or less, Si greater than 0 mass% and 5 mass% or less, and residual Ni in a greater amount than other components, the metal structure of the coating comprises a first phase and a second phase, the concentration of P in the first phase is higher than the average concentration of P in the entire Ni-based self-fluxing alloy, the concentration of P in the second phase is lower than the concentration of P in the first phase, and in an image of the metal structure on the surface of the coating observed under a microscope, the area ratio range of the second phase in a 10 μm square area is 0 to 0.7.

[0008] According to this embodiment, in a glass manufacturing component having a coating formed from a Ni-based self-fluxing alloy, the wear resistance of the coating can be improved. The inventors of the present invention observed the cross-section of the coating with an optical microscope and an electron microscope and discovered that cracks tend to occur in the first phase. Therefore, by finely dispersing the first phase and the second phase with each other, the area of ​​each individual first phase can be reduced. This makes it possible to suppress the propagation of cracks that occur in the first phase and improve the wear resistance of the coating.

[0009] In the above embodiment, in the image obtained by observing the metallic structure on the surface of the coating under a microscope, the coefficient of variation of the area ratio of the second phase in the 10 μm square region may be 0 or more and 0.25 or less. Furthermore, the Ni-based self-fluxing alloy may further contain hard particles greater than 0 mass% and 15.7 mass% or less. Also, the B content of the Ni-based self-fluxing alloy may be 0.5 mass% or less. The main body may be formed of cast iron.

[0010] Another aspect of the present invention relates to a method for manufacturing a glass manufacturing component for conveying or shaping glass having a viscosity logη = 3 to 14.6, comprising: a coating formation step of thermal spraying a Ni-based self-fluxing alloy containing P greater than 0% by mass and 3% by mass or less, Si greater than 0% by mass and 5% by mass or less, and Ni in a larger amount than other components as residue, onto a body made of metal to form a coating of the Ni-based self-fluxing alloy on the surface of the body; and a heat treatment step of heat treating the body and the coating at a maximum temperature of 700°C to 1060°C.

[0011] According to this embodiment, a method for manufacturing glass manufacturing components having a highly abrasion-resistant coating can be provided. In the heat treatment process, by heat-treating the main body and the coating at a maximum temperature of 700°C to 1060°C, the adhesion between the coating and the component can be improved, and the aggregation of the first phase can be suppressed, maintaining the first and second phases in a dispersed state. As a result, the area of ​​each individual first phase is reduced, and the propagation of cracks is suppressed. This improves the abrasion resistance of the coating.

[0012] In the above embodiment, the main body and the coating may be heat-treated at a maximum temperature of 700°C to 980°C during the heat treatment step. [Effects of the Invention]

[0013] According to the above embodiments, the wear resistance of the coating formed from a Ni-based self-fluxing alloy can be improved in a glass manufacturing component. Furthermore, a method for manufacturing a glass manufacturing component having a coating with high wear resistance can be provided.

Brief Description of Drawings

[0014] [Figure 1] Explanatory drawing showing an example of a member for glass manufacturing [Figure 2] Cross-sectional view of a member for glass manufacturing [Figure 3] Image of the surface of a coating obtained by a scanning electron microscope [Figure 4] Si distribution image of the cross-section of a coating obtained by scanning electron microscope energy dispersive X-ray spectroscopy [Figure 5] P distribution image of the cross-section of a coating obtained by scanning electron microscope energy dispersive X-ray spectroscopy [Figure 6] Si and P distribution images of the cross-section of a coating obtained by scanning electron microscope energy dispersive X-ray spectroscopy [Figure 7] Graph showing the Si and P concentrations of the first phase and the second phase [Figure 8] Graph showing the load-unload curves of the first phase and the second phase obtained by a ultra microhardness tester [Figure 9] Graph showing the converted Vickers hardness and the plastic deformation ratio of the indentation work of the first phase and the second phase [Figure 10] Explanatory drawing showing the definition of the plastic deformation ratio of the indentation work [Figure 11] Graph showing the results of differential scanning calorimetry (DSC) of the Ni-based self-fluxing alloy used for Samples 1-9 [Figure 12] Explanatory drawing showing the heating profile of the heat treatment [Figure 13] Optical microscope images of the surfaces of the coatings 12 of Samples 1, 5, and 9 [Figure 14] (A1, B1, C1) Electron microscope images of the surfaces of the coatings 1 of Samples 1, 5, and 9, (A2, B2, C2) Processed images of the optical microscope images [Figure 15] (A) Diagram dividing the processed image of Sample 5 into a 10 μm square mesh, (B) Table showing the area ratio of the first phase in each mesh [Figure 16](A) A diagram showing the processed image of sample 9 divided into 10 μm square meshes, (B) A table showing the area ratio of the second phase in each mesh. [Figure 17] Graph showing the area ratio range for samples 1, 3-9. [Figure 18] Graph showing the coefficient of variation of the area proportions for samples 1, 3-9. [Figure 19] Graph showing the results of the MSE test. [Figure 20] (A) Electron microscope image of the cross-section of sample 4, and (B) Graph showing the concentration distribution of Fe and Ni in the thickness direction. [Figure 21] (A) Electron microscope image of a cross-section of sample 1, and (B) Graph showing the concentration distribution of Fe and Ni in the thickness direction. [Figure 22] Graph showing the interface thickness of samples 1-8. [Modes for carrying out the invention]

[0015] The following describes an embodiment of the glass manufacturing component. The glass manufacturing component has a viscosity of logη = 3 to 14.6 (= 10 3 ~10 14.6 It is used to transport or shape glass. Here, logη is the common logarithm. As shown in Figure 1, the glass manufacturing component 1 includes a glass bottle molding mold 2 for shaping glass bottles from molten glass, and a glass block transport component 4 for transporting molten glass blocks (gobs) supplied from the molten glass tank 3 to the mold 2. The mold 2 includes a rough mold, baffles, mouth mold, plunger for shaping parisons from molten glass blocks, and a finishing mold for shaping glass bottles from parisons. The glass block transport component 4 includes chutes and troughs for transporting gobs to the rough mold. The glass block transport component 4 also includes scoops, troughs, and deflectors. The glass manufacturing component 1 also includes press molding dies, molding rolls, transport rolls, and jigs that come into contact with the transport mold and glass.

[0016] The glass may be, for example, soda-lime glass, borosilicate glass, lead glass, etc. The glass in contact with the glass manufacturing component 1 should preferably be between 400°C and 1400°C.

[0017] As shown in Figure 2, the glass manufacturing component 1 has a body 11 made of metal and a coating 12 formed on the surface of the body 11 by a Ni-based self-fluxing alloy. The body 11 may be made of cast iron, aluminum alloy, etc. The coating 12 is formed by thermal spraying and heat treatment of a Ni-based self-fluxing alloy.

[0018] Ni-based self-fluxing alloys contain phosphorus (P) in amounts greater than 0% by mass and less than or equal to 3% by mass, silicon (Si) in amounts greater than 0% by mass and less than or equal to 5% by mass, and residual nickel (Ni) in amounts greater than other components. The Si content in Ni-based self-fluxing alloys may be between 2% by mass and 5% by mass, or between 3% by mass and 5% by mass. The P content in Ni-based self-fluxing alloys may be between 1% by mass and 2% by mass, or between 1.5% by mass and 2% by mass. The Ni content in Ni-based self-fluxing alloys may be between 50% by mass and 90% by mass, or between 60% by mass and 80% by mass.

[0019] The B content of the Ni-based self-fluxing alloy is preferably 0.5% by mass or less. Preferably, the B content of the Ni-based self-fluxing alloy is 0.1% by mass or less. The B content of the Ni-based self-fluxing alloy may be 0% by mass.

[0020] B and Si are flux components, and the higher their content, the better the self-fluxability of the Ni-based self-flux alloy. B and Si form B2O3 and SiO2 oxide films on the surface of the Ni-based self-flux alloy. Since B2O3 can enhance adhesion to molten glass, a lower B content is preferable in the Ni-based self-flux alloy according to this embodiment.

[0021] P is added to lower the melting point of Ni-based self-fluxing alloys. Similar to B, a flux component, it is known that adding P to Ni lowers its melting point. In the Ni-based self-fluxing alloy according to this embodiment, a low B content is preferable, but if the amount of B added is too low, the melting point of the Ni-based self-fluxing alloy will not be sufficiently lowered, making it difficult to improve the adhesion of the coating by heat treatment.

[0022] Ni-based self-fluxing alloys may further contain hard particles in an amount greater than 0% by mass and less than or equal to 15.7% by mass. These hard particles are dispersed within the Ni-based self-fluxing alloy base material, improving the wear resistance of the Ni-based self-fluxing alloy. Hard particles include carbides, nitrides, oxides, and so-called cermet materials, which are composites of these with metallic materials. Ni-based self-fluxing alloys contain at least one of carbides, nitrides, oxides, and cermets as hard particles. The hard particle content may be greater than 0% by mass and less than 5% by mass. While increasing the hard particle content improves wear resistance, too much hard particle content makes machining and other processes during component manufacturing difficult. Furthermore, a higher hard particle content makes the Ni-based self-fluxing alloy more easily adhered to molten glass ingots. Therefore, if prioritizing a reduced adhesion of the Ni-based self-fluxing alloy to molten glass ingots, a lower hard particle content is preferable, and it may even be 0%.

[0023] Carbides as hard particles include carbides of any one element from Groups 4, 5, and 6 of the periodic table, such as TiC (titanium carbide), ZrC (zirconium carbide), HfC (hafnium carbide), VC or V2C (vanadium carbide), NbC (niobium carbide), TaC (tantalum carbide), Cr3C2, Cr7C3, or Cr 23 Contains C6 (chromium carbide), Mo2C (molybdenum carbide), WC or W2C (tungsten carbide), etc.

[0024] Furthermore, the carbide as hard particles may be silicon carbide.

[0025] The oxide as hard particles may contain an oxide of at least one metal selected from lanthanides. The oxide of at least one metal selected from lanthanides may be cerium oxide.

[0026] The cermet may contain a carbide of any one of the elements from groups 4, 5, and 6 of the periodic table. The cermet particles, which are composites of the above carbide and a metallic material, are preferably WC (WC-12%Co) containing 12% by mass of Co (cobalt) as a binder, but are not limited thereto.

[0027] Ni-based self-fluxing alloys may contain at least one metal selected from Groups 4, 5, and 6 of the periodic table. The amount of metal is 0% to 30% by mass, and preferably 2.5% to 10% by mass. Furthermore, the metal is preferably chromium (Cr), and the amount of Cr is preferably 2.5% to 10% by mass.

[0028] Ni-based self-fluxing alloys may contain trace amounts of impurities that are unavoidable during the manufacturing process.

[0029] The manufacturing method for the glass manufacturing component 1 comprises a coating formation step of spraying a Ni-based self-fluxing alloy onto a main body 11 to form a Ni-based self-fluxing alloy coating 12 on the surface of the main body 11, and a heat treatment step of heat treating the main body 11 and the coating 12 at a maximum temperature of 700°C to 1060°C.

[0030] Thermal spraying is preferably carried out by flame spraying. In flame spraying, the Ni-based self-fluxing alloy is melted by the combustion flame of oxygen and fuel, and the molten Ni-based self-fluxing alloy is sprayed onto the main body 11 of the glass manufacturing component 1. The Ni-based self-fluxing alloy is preferably prepared in the form of powder, wire, rod, etc., and supplied to the thermal spraying apparatus. Thermal spraying is preferably, for example, HVOF (High Velocity Oxygen Fuel) spraying, but it is not limited to this method.

[0031] In the heat treatment process, the main body 11 and the coating 12 are heat-treated at a maximum temperature of 700°C to 1060°C. Alternatively, in the heat treatment process, the main body 11 and the coating 12 may be heat-treated at a maximum temperature of 700°C to 980°C. Alternatively, in the heat treatment process, the main body 11 and the coating 12 may be heat-treated at a maximum temperature of 700°C to 900°C.

[0032] During the heat treatment, the body 11 and the coating 12 diffuse from each other at the interface between them. This improves the adhesion between the body 11 and the coating 12, and suppresses the peeling of the coating 12 from the body 11.

[0033] The microstructure of the coating 12 includes a first phase and a second phase. The concentration of phosphorus (P) in the first phase is higher than the average concentration of P in the entire Ni-based self-fluxing alloy. The concentration of P in the second phase is lower than the concentration of P in the first phase. Furthermore, the concentration of P in the second phase is lower than the average concentration of P in the entire Ni-based self-fluxing alloy. In a microscopic image of the microstructure of the surface of the coating 12, the area ratio of the second phase in a 10 μm square area is between 0 and 0.7. Also, in a microscopic image of the microstructure of the surface of the coating 12, the coefficient of variation of the area ratio of the second phase in a 10 μm square area is between 0 and 0.25. The microscope may be an optical microscope or an electron microscope.

[0034] The glass manufacturing component 1 according to this embodiment was created based on the following concept. The inventors of this application observed a cross-section of the coating 12 of the glass manufacturing component 1, which has a cast iron body 11 and a coating 12 made of a Ni-based self-fluxing alloy, using an electron microscope and discovered that cracks were more likely to occur in the first phase than in the second phase. The composition of the Ni-based self-fluxing alloy used was 5 mass% Si, 1.6 mass% P, 4.5 mass% Cr, 71.2 mass% Ni, 2.0 mass% Mo, and 15.7 mass% WC-12%Co. The heat treatment after thermal spraying was performed at a maximum temperature of 1100°C.

[0035] Figure 3 is an image of the surface of coating 12 acquired by scanning electron microscopy (SEM). Figure 4 is a Si distribution image of the surface of coating 12 acquired by scanning electron microscopy-energy dispersive X-ray spectrometry (SEM-EDS). Figure 5 is a P distribution image acquired by scanning electron microscopy-energy dispersive X-ray spectrometry. Figure 6 is a distribution image of Si and P acquired by scanning electron microscopy-energy dispersive X-ray spectrometry. Figures 3 to 6 are images of the same region. Note that a dashed line has been added to Figure 6 to emphasize the boundary between the first and second phases. From Figures 3 to 6, it can be seen that the metallographic structure on the surface of coating 12 contains a first phase and a second phase with different concentrations of P and Si. It can also be seen that cracks are more concentrated in the first phase than in the second phase. Furthermore, it can be seen that the cracks extend continuously in the first phase.

[0036] Figure 7 is a graph showing the Si and P concentrations in the first and second phases. The Si and P concentrations were obtained by scanning electron microscopy energy-dispersive X-ray spectroscopy as shown in Figure 6. From Figure 6, it can be seen that the P concentration in the first phase is higher than the average P concentration of the entire Ni-based self-fluxing alloy (the P concentration of the Ni-based self-fluxing alloy itself) and also higher than the P concentration in the second phase. Furthermore, the P concentration in the second phase is lower than the average P concentration of the entire Ni-based self-fluxing alloy.

[0037] Figure 8 is a graph showing the loading-unloading curves of the first and second phases obtained by an ultramicrohardness tester. Figure 9 shows the converted Vickers hardness [HV] of the first and second phases. *This is a graph showing the plastic deformation ratio ηit[%] of the work of indentation. The plastic deformation ratio ηit[%] of the work of indentation in Figure 9 is obtained from the loading-unloading curve in Figure 8 based on the definition shown in Figure 10, as specified in ISO 14577-1:2015 "Metallic materials - Instrumented indentation hardness test and material parameters - Part 1: Test methods Annex A". The converted Vickers hardness is similarly obtained from the method specified in ISO 14577-1:2015 "Metallic materials - Instrumented indentation hardness test and material parameters - Part 1: Test methods Annex A". As a result, it can be seen that the first phase is harder and has elastic properties compared to the second phase. In other words, it can be seen that the first phase is less susceptible to compositional deformation and is more brittle than the second phase. In other words, it can be seen that the first phase has properties closer to ceramics than to metals compared to the second phase.

[0038] Based on the above, the first phase, which has a higher P concentration than the second phase, is brittle and prone to cracking. Therefore, when the first phase accumulates, long cracks are more likely to form. By reducing the area proportion of the first phase, the region prone to cracking can be reduced. In addition, by dispersing the first and second phases, the length of each crack can be suppressed. [Examples]

[0039] Samples 1-9 were prepared and evaluated under different heat treatment conditions. Sample 1-7 is an embodiment of the present invention, and samples 8-9 are comparative examples. In samples 1-9, the composition and shape of the main body 11 and the coating 12 are identical. The main body 11 is a plate made of cast iron. The composition of the Ni-based self-fluxing alloy used to form the coating 12 was 5 mass% Si, 1.6 mass% P, 4.5 mass% Cr, 71.2 mass% Ni, 2.0 mass% Mo, and 15.7 mass% WC-12%Co (particle size 15-45 μm, U-Tech Japan Co., Ltd.). The heat treatment conditions for samples 1-9 are shown in Table 1. [Table 1]

[0040] Figure 11 is a graph showing the differential scanning calorimetry (DSC) results for the Ni-based autoflux alloys used in samples 1-9. From Figure 11, it can be seen that the Ni-based autoflux alloys begin to melt at 1080°C. The melting peak was at 1237°C.

[0041] The method for forming coating 12 is shown in Table 2 below. As alloy raw materials, metal powders with the composition and particle size (median diameter) determined by ICP emission spectroscopy and laser diffraction / scattering methods were prepared by gas atomization, and these powders were mixed with WC-12%Co. The mixed powder was then sprayed onto the surface of gray cast iron by high-velocity flame spraying (HVOF (High Velocity Oxygen Fuel) method) to form a Ni-based alloy coating with a thickness of approximately 0.8 mm, which was used as a test specimen. [Table 2]

[0042] The heat treatment of the main body 11 and coating 12 after thermal spraying was performed using an electric furnace. Each sample 1-9 was heated based on the heating profile shown in Figure 12. The preheating temperature, preheating time, heating temperature, and heating time for each sample 1-9 are shown in Table 1. In the heat treatment of each sample 1-9, the heating rate from room temperature to preheating temperature was 400°C / min, the heating rate from preheating temperature to heating temperature was 200°C / min, and the cooling rate from heating temperature to room temperature was 400°C / min. Note that all temperatures are the ambient temperatures inside the electric furnace.

[0043] Figure 13 shows optical microscope images of the surface of coating 12 for samples 1, 5, and 9. The results for sample 1, which was not heat-treated, show that the first and second phases are present even without heat treatment. In sample 5, which was heated at 980°C, the first and second phases are finely dispersed, similar to sample 1. In sample 9, which was heated at 1080°C, the first phase is aggregated and coarser compared to sample 5.

[0044] Figure 14 shows optical microscope images of the surface of coating 12 of samples 1, 5, and 9 (A1, B1, C1) and processed images of the optical microscope images (A2, B2, C2). The processed images are obtained by processing the optical microscope images with a predetermined image processing application. In the processed images, the contrast between the first and second phases is enhanced. In the processed images, the first part is displayed darker, and the second part is displayed lighter. Also, in the processed images, areas where WC has aggregated are displayed in white, distinguishing them from the first and second phases.

[0045] Figure 15(A) shows the processed image of sample 5 divided into 10 μm square meshes, and (B) is a table showing the area ratio of the first phase in each mesh. Figure 16(A) shows the processed image of sample 9 divided into 10 μm square meshes, and (B) is a table showing the area ratio of the second phase in each mesh. Each processed image is divided into 9 sections in the y direction (vertical direction) and 12 sections in the x direction (horizontal direction), resulting in 108 meshes.

[0046] The area ratio of the first phase in each mesh is obtained using an image processing application. The image processing application obtains the number of pixels corresponding to the second phase for each mesh, and then divides the obtained number of pixels corresponding to the second phase by the number of pixels contained in a 10 μm square mesh to obtain the area ratio of the first phase in each mesh.

[0047] Figure 17 is a graph showing the range of area percentages for samples 1 and 3-9. The range of area percentages is the difference between the maximum and minimum area percentages for each sample. The more dispersed the first and second phases are, the more equal the area percentages of each mesh become. Therefore, the more dispersed the first and second phases are, the smaller the range of area percentages becomes. In other words, the range of area percentages represents the degree of dispersion of the first and second phases. As shown in Figure 17, the range of area percentages increases as the heating temperature increases. In other words, it can be seen that the first phase is more aggregated as the heating temperature increases.

[0048] Figure 18 is a graph showing the coefficient of variation of the area proportions for samples 1 and 3-9. The coefficient of variation (CV) of the area proportion is the value obtained by dividing the standard deviation (σ) of the area proportion by the mean (A) of the area proportion for each sample (CV = σ / A). The more dispersed the first and second phases are, the more equal the area proportions of each mesh become. Therefore, the more dispersed the first and second phases are, the smaller the coefficient of variation of the area proportion becomes. In other words, the coefficient of variation of the area proportion represents the degree of dispersion of the first and second phases. As shown in Figure 18, the coefficient of variation of the area proportion increases as the heating temperature increases. In other words, the first phase is more aggregated as the heating temperature increases.

[0049] Figure 19 is a graph showing the results of the microslurry jet erosion test (MSE). The MSE test was performed using MSE-A from Parmeso Co., Ltd. The particles used were polygonal alumina GA1 with an average particle size of 1.2 μm. The slurry concentration was 3 mass%. The projection force was set so that the erosion force was 6.36 μm / g, with Si as the calibration material. A higher MSE resistance value [g / μm] indicates higher abrasion resistance. As shown in Figure 19, the MSE resistance value decreases as the heating temperature increases. In other words, abrasion resistance decreases as the heating temperature increases.

[0050] From the viewpoint of wear resistance, it is preferable that the MSE resistance value is greater than 1 g / μm. Therefore, it is preferable that the heating temperature is 1060°C or lower. Furthermore, it is preferable that the MSE resistance value is greater than 1.5 g / μm. In this case, it is preferable that the heating temperature is 980°C or lower. Furthermore, it is preferable that the MSE resistance value is greater than 1.8 g / μm. In this case, it is preferable that the heating temperature is 800°C or lower.

[0051] Samples 1 to 7 are preferred because their MSE resistance values ​​are greater than 1 g / μm. Therefore, as shown in Figure 17, it is preferable that the area ratio of the second phase in a 10 μm square region in the image of the metal structure observed with an optical microscope is between 0 and 0.7. More preferably, the area ratio of the second phase in a 10 μm square region in the image of the metal structure observed with an optical microscope is between 0 and 0.6. Even more preferably, the area ratio of the second phase in a 10 μm square region in the image of the metal structure observed with an optical microscope is between 0 and 0.5.

[0052] Furthermore, as shown in Figure 18, in the image of the metal structure observed with an optical microscope, the coefficient of variation of the area ratio of the second phase in a 10 μm square region is preferably 0 or more and 0.25 or less. More preferably, in the image of the metal structure observed with an optical microscope, the coefficient of variation of the area ratio of the second phase in a 10 μm square region is preferably 0 or more and 0.2 or less. Even more preferably, in the image of the metal structure observed with an optical microscope, the coefficient of variation of the area ratio of the second phase in a 10 μm square region is preferably 0 or more and 0.15 or less.

[0053] Figure 20 shows (A) an electron microscope image of the cross-section of sample 4, and (B) a graph showing the concentration distribution of Fe and Ni in the thickness direction. The concentration distribution of Fe and Ni in the thickness direction of the cross-section of sample 4 was measured by SEM-EDS. In sample 4, which was heated at a temperature of 900°C, the concentration of Fe decreases and the concentration of Ni increases from the body 11 side to the coating 12 side at the interface between the body 11 and the coating 12. That is, it can be seen that sample 4 has an interface where Fe and Ni are diffused. The thickness of the interface in sample 4 is approximately 20 μm.

[0054] Figure 21 shows (A) an electron microscope image of the cross-section of Sample 1, and (B) a graph showing the concentration distribution of Fe and Ni in the thickness direction. The concentration distribution of Fe and Ni in the thickness direction of the cross-section of Sample 1 was measured by SEM-EDS. In Sample 1, where heat treatment was omitted, there is a rapid change in Fe and Ni at the interface between the main body 11 and the coating 12. In Sample 1, the interface thickness is approximately 3 μm.

[0055] Figure 22 is a graph showing the interface thickness for samples 1-8. From sample 1-6, it can be seen that the interface thickness increases as the heating temperature increases. However, from samples 6-8, it can be seen that at heating temperatures of 1030°C or higher, the interface thickness does not increase even as the temperature rises. From the viewpoint of adhesion between the coating 12 and the main body 11, it is preferable that the interface thickness be 10 μm or more. Therefore, it is preferable that the heating temperature be 800°C or higher.

[0056] This concludes the description of specific embodiments, but the present invention is not limited to the above embodiments and can be broadly modified and implemented. [Explanation of symbols]

[0057] 1: Components for glass manufacturing 2: Mold 3: Molten glass bath 4: Components for transporting glass blocks 11: Main unit 12:Coating

Claims

1. A glass manufacturing component for conveying or shaping glass with a viscosity logη = 3 to 14.6, A body made of metal, It has a coating formed on the surface of the main body by a Ni-based self-fluxing alloy, The Ni-based self-fluxing alloy contains P greater than 0% by mass and 3% by mass or less, Si greater than 0% by mass and 5% by mass or less, and Ni in a larger amount than other components as residue. The metallic structure of the aforementioned coating comprises a first phase and a second phase. The concentration of P in the first phase is higher than the average concentration of P in the entire Ni-based self-fluxing alloy. The concentration of P in the second phase is lower than the concentration of P in the first phase. A glass manufacturing component wherein, in an image obtained by observing the metallic structure on the surface of the coating under a microscope, the area ratio of the second phase in a 10 μm square region is between 0 and 0.

7.

2. The glass manufacturing component according to claim 1, wherein, in an image obtained by observing the metallic structure on the surface of the coating under a microscope, the coefficient of variation of the area ratio of the second phase in the 10 μm square region is 0 or more and 0.25 or less.

3. The glass manufacturing component according to claim 2, wherein the Ni-based self-fluxing alloy further comprises hard particles greater than 0% by mass and 15.7% by mass or less.

4. The glass manufacturing component according to claim 3, wherein the B content of the Ni-based self-fluxing alloy is 0.5% by mass or less.

5. The glass manufacturing member according to claim 4, wherein the main body is formed of cast iron.

6. A method for manufacturing glass manufacturing components for conveying or shaping glass with a viscosity of logη = 3 to 14.6, A coating formation step involves thermal spraying a Ni-based self-fluxing alloy containing P greater than 0% by mass and 3% by mass or less, Si greater than 0% by mass and 5% by mass or less, and Ni in a larger amount than other components as residue, onto a metal body to form a coating of the Ni-based self-fluxing alloy on the surface of the body. A method for manufacturing glass components, comprising a heat treatment step of heat-treating the main body and the coating at a maximum temperature of 700°C to 1060°C.

7. The method for manufacturing a glass manufacturing component according to claim 6, wherein in the heat treatment step, the main body and the coating are heat-treated at a maximum temperature of 700°C to 980°C.

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