Glass-manufacturing member and method for manufacturing same

Abstract

[Problem] To improve the wear resistance of a coating film, which is formed of a Ni-based self-fluxing alloy, in a glass-manufacturing member having the coating film. [Solution] A glass-manufacturing member 1 for conveying or forming glass having a viscosity of logη=3 to 14.6, includes: a body 11 formed of a metal; and a coating film 12 composed of an Ni-based self-fluxing alloy and formed on the surface of the body. The Ni-based self-fluxing alloy contains more than 0 mass% and not more than 3 mass% of P, more than 0 mass% and not more than 5 mass% of Si, and Ni as the remainder in an amount greater than the other components. The metal structure of the coating film 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 obtained by observing the metal structure with a microscope, the range of the area ratio of the second phase in a 10-µm-square region is 0-0.7.

Description

Glass manufacturing components and methods for manufacturing the same

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

[0002] In the glass molding process, if the glass manufacturing components and the glass at a high temperature adhere easily, molding defects can occur, such as inaccurate shaping of the product or scratches on the surface of the glass product. Therefore, for example, in the molding of glass bottles, a release agent is frequently applied (called swab) to ensure release properties. In the following text, glass at a high temperature that is suitable for molding is referred to as glass with a viscosity of logη = 3 to 14.6 (= 10 ３ ~10 １４．６ Glass in a poise state and its lumps are defined as "molten glass" or "molten glass lumps." Here, logη is the common logarithm.

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

[0004] Specification of Japanese Patent No. 7142159

[0005] The inventors of this application 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.

[0007] One aspect of the present invention is a glass manufacturing member (1) for transporting 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% by mass and 3% by mass or less, Si greater than 0% by mass and 5% by 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 an image obtained by microscopic observation of the metallic structure on the surface of the coating, 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. Furthermore, 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 metal body 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 phase and the second phase 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.

[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.

[0014] Diagram illustrating an example of a glass manufacturing component. Cross-sectional view of a glass manufacturing component. Image of the surface of the coating obtained by scanning electron microscopy. Si distribution image of the cross-section of the coating obtained by scanning electron microscopy energy-dispersive X-ray spectroscopy. P distribution image of the cross-section of the coating obtained by scanning electron microscopy energy-dispersive X-ray spectroscopy. Distribution images of Si and P in the cross-section of the coating obtained by scanning electron microscopy energy-dispersive X-ray spectroscopy. Graph showing the Si and P concentrations of the first and second phases. Graph showing the loading-unloading curves of the first and second phases obtained by an ultramicrohardness tester. Graph showing the plastic deformation ratio of the converted Vickers hardness and indentation work of the first and second phases. Diagram illustrating the definition of the plastic deformation ratio of the indentation work. Graph showing the differential scanning calorimetry (DSC) results of the Ni-based self-fluxing alloy used in Sample 1-9. Diagram illustrating the heating profile of the heat treatment. Sample 1, Optical microscope images of the surface of coating 12 of samples 5 and 9 (A1, B1, C1) Electron microscope images of the surface of coating 12 of samples 1, 5 and 9 (A2, B2, C2) Processed images of the optical microscope images (A) Diagram dividing the processed image of sample 5 into 10 μm square meshes, (B) Table showing the area ratio of the first phase in each mesh (A) Diagram dividing the processed image of sample 9 into 10 μm square meshes, (B) Table showing the area ratio of the second phase in each mesh Graph showing the range of area ratios of samples 1, 3-9 Graph showing the coefficient of variation of the area ratios of samples 1, 3-9 Graph showing the results of the MSE test (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 (A) Electron microscope image of the cross-section of sample 1, and (B) Graph showing the concentration distribution of Fe and Ni in the thickness direction Graph showing the interface thickness of samples 1-8

[0015] The following describes an embodiment of a glass manufacturing component. The glass manufacturing component has a viscosity of logη = 3 to 14.6 (= 10 ３ ~10 １４．６It is used to transport or shape glass (poise). 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. Furthermore, the glass manufacturing component 1 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) greater than 0% by mass and 3% by mass or less, silicon (Si) greater than 0% by mass and 5% by mass or less, and residual nickel (Ni) in a larger amount than other components. The Si content in Ni-based self-fluxing alloys may be 2% by mass or more and 5% by mass or less, or 3% by mass or more and 5% by mass or less. The P content in Ni-based self-fluxing alloys may be 1% by mass or more and 2% by mass or less, or 1.5% by mass or more and 2% by mass or less. The Ni content in Ni-based self-fluxing alloys may be 50% by mass or more and 90% by mass or less, or 60% by mass or more and 80% by mass or less.

[0019] The content of B in the Ni-based self-fluxing alloy is preferably 0.5% by mass or less. More preferably, the content of B in the Ni-based self-fluxing alloy is 0.1% by mass or less. The content of B in 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-fluxing property of the Ni-based self-fluxing alloy. B and Si form B ２ O ３ and SiO ２ oxide films on the surface of the Ni-based self-fluxing alloy. B ２ O ３ can be a factor that enhances the adhesion to molten glass. Therefore, in the Ni-based self-fluxing alloy according to this embodiment, it is preferable that the content of B is less.

[0021] P is added to lower the melting point of the Ni-based self-fluxing alloy. Similar to B which is a flux component, it is known that adding P to Ni lowers the melting point. In the Ni-based self-fluxing alloy according to this embodiment, it is preferable that the content of B is less. However, if the addition amount of B is small, the melting point drop of the Ni-based self-fluxing alloy is not sufficient, and it becomes difficult to improve the adhesion of the coating by heat treatment.

[0022] The Ni-based self-fluxing alloy preferably further contains hard particles greater than 0% by mass and 15.7% by mass or less. The hard particles are dispersed in the base Ni-based self-fluxing alloy and improve the wear resistance of the Ni-based self-fluxing alloy. The hard particles include carbides, nitrides, oxides, and so-called cermet materials which are composites of these and metal materials. The Ni-based self-fluxing alloy contains at least one of carbides, nitrides, oxides, and cermets as hard particles. The content of the hard particles may be greater than 0% by mass and less than 5% by mass. When the content of the hard particles increases, the wear resistance improves, but if it is too much, machining such as cutting when manufacturing the member becomes difficult. Also, when the content of the hard particles increases, the Ni-based self-fluxing alloy becomes more likely to adhere to the molten glass mass. Therefore, when prioritizing reducing the adhesion of the Ni-based self-fluxing alloy to the molten glass mass, the lower the content of the hard particles, the more preferable, and it may be 0.

[0023] The carbides as hard particles include carbides of any one of the elements in groups 4, 5, and 6 of the periodic table, for example, TiC (titanium carbide), ZrC (zirconium carbide), HfC (hafnium carbide), VC, or V ２ C (vanadium carbide), NbC (niobium carbide), TaC (tantalum carbide), Cr ３ C ２ , Cr ７ C ３ or Cr ２３ C ６ (Chromium carbide), Mo ２ C (molybdenum carbide), WC or W ２ Contains C (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 a composite of the above carbide and a metal 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 the 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 the 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) thermal 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 member 1 according to the embodiment is created based on the following idea. When the inventors of the present application observed the cross-section of the coating 12 of the glass manufacturing member 1 having the cast iron main body 11 and the coating 12 made of a Ni-based self-fluxing alloy with an electron microscope, they found that cracks are 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% by mass of Si, 1.6% by mass of P, 4.5% by mass of Cr, 71.2% by mass of Ni, 2.0% by mass of Mo, and 15.7% by mass of WC-12% Co. The heat treatment after spraying had a maximum temperature of 1100°C.

[0035] FIG. 3 is an image of the surface of the coating 12 obtained by a scanning electron microscope (Scanning Electron Microscopy: SEM). FIG. 4 is an Si distribution image of the surface of the coating 12 obtained by scanning electron microscope-energy dispersive X-ray spectrometry (Scanning Electron Microscopy-Energy dispersive X-ray spectrometry: SEM-EDS). FIG. 5 is a P distribution image obtained by scanning electron microscope-energy dispersive X-ray spectrometry. FIG. 6 is a distribution image of Si and P obtained by scanning electron microscope-energy dispersive X-ray spectrometry. FIGS. 3 to 6 are images of the same region. In FIG. 6, a broken line is added to emphasize the boundary between the first phase and the second phase. From FIGS. 3 to 6, it can be seen that the metal structure on the surface of the coating 12 includes a first phase and a second phase with different concentrations of P and Si. Also, it can be seen that the cracks are more concentrated in the first phase than in the second phase. Also, it can be seen that the cracks extend continuously in the first phase.

[0036] FIG. 7 is a graph showing the concentrations of Si and P in the first phase and the second phase. The concentrations of Si and P are obtained by scanning electron microscope-energy dispersive X-ray spectrometry of FIG. 6. From FIG. 6, it can be seen that 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 Ni-based self-fluxing alloy itself) and higher than the concentration of P in the second phase. Also, the concentration of P in the second phase is lower than the average concentration of P in the entire Ni-based self-fluxing alloy.

[0037] Figure 8 is a graph showing the load-unload curves of the first phase and the second phase obtained by a microhardness tester. Figure 9 is a graph showing the converted Vickers hardness [HV ＊ and the plastic deformation ratio ηit [%] of the indentation work. The plastic deformation ratio ηit [%] of the indentation work in Figure 9 is obtained from the load-unload curve in Figure 8 based on the definition shown in Figure 10, which is specified in ISO 14577-1:2015 "Metallic materials - Instrumented indentation hardness testing and materials 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 testing and materials parameters - Part 1: Test methods Annex A". As a result, it can be seen that the first phase is harder than the second phase and has elastic properties. That is, it can be seen that the first phase is less likely to undergo compositional deformation and is brittle compared to the second phase. That is, it can be seen that the first phase has properties closer to ceramics than metals compared to the second phase.

[0038] From the above, the first phase with a higher P concentration than the second phase is brittle and prone to crack generation. Therefore, when the first phase aggregates, long cracks are likely to occur. Therefore, by reducing the area ratio of the first phase, the area where cracks are likely to occur can be reduced. Also, by dispersing the first phase and the second phase, the length of each crack can be suppressed.

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

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

[0041] The method for forming the 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.

[0042] The heat treatment of the main body 11 and the coating 12 after thermal spraying was performed using an electric furnace. Each sample 1-9 was heated according to 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 the preheating temperature was 400°C / min, the heating rate from the preheating temperature to the heating temperature was 200°C / min, and the cooling rate from the 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 the coating 12 for samples 1, 5, and 9. From the results for sample 1, which was not heat-treated, it can be seen 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 the 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, the parts 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 value (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, it can be seen that 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, it is preferable that the coefficient of variation of the area ratio of the second phase in a 10 μm square region is between 0 and 0.25. 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 between 0 and 0.2. 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 between 0 and 0.15.

[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 of 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 rises. 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.

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

Claims

1. A glass manufacturing component for transporting or shaping glass having a viscosity logη = 3 to 14.6, comprising a body made of metal and a coating 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% by mass and 3% by mass or less, Si greater than 0% by mass and 5% by 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 or more and 0.7 or less.

2. The glass manufacturing member 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 a glass manufacturing component for transporting 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 metal body 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.

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 or more and 980°C or less.

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