A strong broadband absorption glass, its preparation method and application

Abstract

The present application relates to special glass material, especially to a kind of strong wide spectrum absorption glass and its preparation method and application.Including the following elements by mole fraction:Si 12-15 parts, B 6-8 parts, Al 0.5-1 part, Na 6-8 parts, K 5-8 parts, Ca 2-3 parts, Ti 1-2 parts, Fe 1-2 parts, Co 4-6 parts, Ni 1-2.5 parts, Mn 0-0.1 part, Cu 0.2-0.5 part, Cr 0.3-1 part, Ce 0.2-0.4 part;Wherein, the sum of mole fraction of Si, B, Al, Ca and Ti is 24-26.5 parts.The glass material provided by the present application has excellent wide spectrum absorption performance, high temperature component stability, good thermal performance and chemical stability, which is beneficial to the industrial large-scale production of light absorption material glass silk.

Description

Technical Field

[0001] This invention relates to special glass materials, and in particular to a strong broadband absorbing glass, its preparation method, and its applications. Background Technology

[0002] The information disclosed in this background section is intended only to enhance understanding of the overall background of the invention and is not necessarily to be construed as an admission or in any way implying that such information constitutes prior art known to those skilled in the art.

[0003] In the field of fiber optic imaging, stray light inevitably arises during image transmission from imaging elements such as optical fiber panels, fiber optic image converters, fiber optic tapers, and fiber optic microlens arrays. This stray light primarily originates from crosstalk between optical fibers, and the interference of crosstalk during image transmission severely affects the image sharpness and contrast of the optical elements.

[0004] Typically, light-absorbing glass fibers are filled into the gaps between adjacent optical fibers to absorb stray light and solve the crosstalk problem in imaging elements. Therefore, the absorption effect of light-absorbing glass on interfering stray light has a direct impact on the final image quality. However, complete optical insulation is currently not achievable. In recent years, with the continuous expansion and deepening of the application scenarios and fields of fiber optic imaging elements, the demand for high-definition, high-contrast fiber optic imaging elements has been increasing, urgently requiring further improvement in the absorption effect of light-absorbing glass on stray light, especially stray light in the visible light band. Summary of the Invention

[0005] To address the shortcomings of existing technologies, the purpose of this invention is to provide a strong broadband absorption glass, its preparation method, and its applications. The glass material provided by this invention has excellent broadband absorption performance, high-temperature component stability, and good thermal and chemical stability, which is beneficial for large-scale industrial production of light-absorbing glass fibers.

[0006] To achieve the above objectives, the present invention is implemented through the following technical solution:

[0007] In a first aspect, the present invention provides a strong broad-spectrum absorption glass, comprising the following elements in a molar fraction meter: The composition is as follows: Si 12-15 parts, B 6-8 parts, Al 0.5-1 parts, Na 6-8 parts, K 5-8 parts, Ca 2-3 parts, Ti 1-2 parts, Fe 1-2 parts, Co 4-6 parts, Ni 1-2.5 parts, Mn 0-0.1 parts, Cu 0.2-0.5 parts, Cr 0.3-1 parts, Ce 0.2-0.4 parts; wherein the sum of the molar parts of Si, B, Al, Ca and Ti is 24-26.5 parts.

[0008] The strong broadband absorption glass described in this invention also includes the essential element oxygen. O is the core element of the glass network forging structure, combining with Si to form silicon-oxygen tetrahedra [SiO4], which constitute the main structure of the glass framework, giving the glass mechanical strength and stability. The introduction of different oxides will change the bridging oxygen ratio in the network structure. The oxygen content directly affects the glass's heat resistance, coefficient of thermal expansion, and other properties.

[0009] In some implementations, the molar fraction of Si is 12.1-15 parts, 12.3-15 parts, 12.7-15 parts, 13-15 parts, 13.3-15 parts, 13.5-15 parts, 13.7-15 parts, 14-15 parts, 14.3-15 parts, 14.5-15 parts, 14.7-15 parts, etc. Si is a glass-forming element, and its structural state in glass plays a decisive role in its properties. Generally, it forms a silicon-oxygen tetrahedral network in glass, becoming the glass's framework. When the Si content is high, it can reduce the coefficient of thermal expansion of the glass, improve its heat resistance, hardness, thermal stability, softening temperature, chemical stability, and mechanical strength, but it can also increase the glass's melting point and viscosity during high-temperature melting, making melting more difficult.

[0010] In some implementations, the molar amounts of boron (B) are 6.3-8 parts, 6.7-8 parts, 6.9-8 parts, 7-8 parts, 7.3-8 parts, 7.5-8 parts, and 7.7-8 parts, respectively. Boron is a glass-forming element, existing in glass as boron-oxygen trigonal [BO3] and boron-oxygen tetrahedral [BO4] structural units, forming a structural network together with silicon-oxygen tetrahedra. Boron can reduce the coefficient of thermal expansion of glass, improve its thermal and chemical stability, increase its refractive index, improve its gloss, and enhance its mechanical properties. Boron can also act as a flux, accelerating the melting and refining of glass. However, when the amount of boron added is too high, the increase in boron-oxygen trigonal units can actually increase the coefficient of thermal expansion of the glass, resulting in boron anomalous phenomena.

[0011] In some implementations, the molar fraction of Al is 0.5-0.9 parts, 0.5-0.8 parts, 0.5-0.7 parts, 0.5-0.6 parts, etc. Al is an intermediate element in glass production. When the molar ratio of sodium to aluminum in the glass is greater than 1, aluminum-oxygen tetrahedra are formed, which together with silicon-oxygen tetrahedra form a continuous structural network. Alumina can reduce the crystallization tendency of glass, improve its chemical stability, refractive index, mechanical strength, thermal stability, hardness, and viscosity, and reduce the erosion of glass on refractory materials.

[0012] In some implementation schemes, the molar amounts of Na are 6-7.7 parts, 6-7.5 parts, 6-7.3 parts, 6-7 parts, 6-6.7 parts, 6-6.5 parts, 6-6.3 parts, etc.

[0013] In some implementation schemes, the molar amounts of K are 5-7.7 parts, 5-7.5 parts, 5-7.3 parts, 5-7 parts, 5-6.7 parts, 5-6.5 parts, 6.1-6.5 parts, 6.1-7.7 parts, 6.1-7.5 parts, 6.1-7.3 parts, 6.1-7 parts, 6.1-6.7 parts, etc.

[0014] Na and K are network elements in glass. Alkali metal elements are easy to move and diffuse in the glass, which can reduce the viscosity of glass during high-temperature melting, making the glass easier to melt. They are good fluxes, but the amount introduced should not be too much. Too much will increase the thermal expansion coefficient of the glass and reduce its chemical stability, thermal stability and mechanical strength.

[0015] In some implementations, the sum of the molar parts of Na and K is no more than 15 parts. The sum of their molar parts can be 12-15 parts, 12-14 parts, 12-13 parts, etc.

[0016] In some implementations, the molar amounts of Ca are 2-2.9 parts, 2-2.6 parts, 2-2.4 parts, 2-2.2 parts, 2-2.1 parts, etc. Ca is a divalent alkaline earth metal element, and its main role in glass is as a stabilizer, increasing the chemical stability and mechanical strength of the glass. However, higher concentrations can increase the glass's tendency to crystallize and make it more brittle. Furthermore, Ca can reduce glass viscosity at high temperatures, promoting melting and refining.

[0017] In some implementations, the molar amounts of Ti are 1-1.9 parts, 1-1.7 parts, 1-1.4 parts, 1-1.2 parts, 1-1.1 parts, etc. Ti can improve the refractive index and chemical stability of borosilicate glasses.

[0018] In some implementations, the sum of the molar parts of Si, B, Al, Ca, and Ti is 25-26.5 parts, 26-26.5 parts, etc.

[0019] In some implementations, the molar fraction of Co is 4.3-6 parts, 4.5-6 parts, 4.7-6 parts, 5-6 parts, 5.3-6 parts, 5.5-6 parts, 5.7-6 parts, 5.9-6 parts, etc. Co has a strong coloring property in glass. In borosilicate glasses, cobalt usually exists stably as divalent cobalt ions, whose absorption band covers the visible light region of 500-800 nm.

[0020] In some implementations, the molar fraction of Ni is 1.1-2.5 parts, 1.3-2.5 parts, 1.5-2.5 parts, 1.7-2.5 parts, 2-2.5 parts, 2.3-2.5 parts, etc. Ni mainly exists as divalent ions in glass. Its absorption characteristics determine the color of the glass: it has a strong absorption band in the visible light range of 400-650 nm, and also has good absorption in the near-infrared range of 650-1000 nm.

[0021] In some implementations, the sum of the molar amounts of Co and Ni is 5-8.5 parts, and can also be 6-8.5 parts, 7-8.5 parts, 8-8.5 parts, etc.

[0022] In some embodiments, the molar fraction of Cu is 0.2-0.45 parts, 0.2-0.4 parts, 0.2-0.35 parts, 0.2-0.3 parts, 0.2-0.27 parts, 0.2-0.25 parts, 0.2-0.22 parts, etc. In glass melted under an oxidizing atmosphere, Cu exists as divalent ions. Divalent copper ions exhibit a strong absorption band in the 700-1100 nm wavelength range, and also show some absorption in the ultraviolet absorption limit down to 700 nm.

[0023] In some implementations, the molar fraction of Cr is 0.3-0.9 parts, 0.3-0.7 parts, 0.3-0.5 parts, 0.3-0.4 parts, etc. In glass, Cr is typically present as the stable Cr... 3+ It exists in this form, and its absorption spectrum exhibits two distinct characteristic absorption peaks around 300-500 nm and 620 nm.

[0024] In some implementations, the sum of the molar parts of Cu and Cr is 0.5-1.5 parts, but it can also be 0.5-1.1 parts, 0.5-1 parts, 0.5-0.9 parts, etc.

[0025] In some implementations, the molar fraction of Fe is 1.1-2 parts, 1.3-2 parts, 1.5-2 parts, 1.7-2 parts, 1.9-2 parts, etc. Iron in glass exists as Fe. 2+ and Fe 3+ Two valence states coexist. Fe 2+ It has strong absorption in the infrared band, while Fe 3+ It absorbs in the ultraviolet region. The combined effect of these two factors results in iron-doped glass exhibiting absorption across a broad spectral range from ultraviolet to infrared, with its near-infrared absorption peak located around 700-1000 nm. Fe 3+ / Fe 2+ The proportion is significantly affected by factors such as melting temperature, atmosphere, glass matrix, and total iron content.

[0026] In some implementations, the molar fraction of Mn is 0.01-0.1 parts, 0.01-0.09 parts, 0.01-0.07 parts, 0.01-0.05 parts, 0.01-0.03 parts, etc. Manganese has a strong coloring ability in glass, and is typically used in the form of Mn. 2+ and Mn 3+ It exists in various forms. Under oxidizing conditions, manganese tends to form trivalent ions (Mn2+). 3+ This ion exhibits strong absorption in the visible light region of 450-600 nm, causing the glass to display a characteristic deep purple color, with the color deepening as the oxidizing atmosphere strengthens. Furthermore, the coloring intensity of manganese can be effectively controlled by adjusting the melting atmosphere.

[0027] In some implementations, the sum of the molar parts of all the coloring ions (Co, Ni, Cu, Cr, Fe, and Mn) is not less than 7.6 parts. Specifically, the sum of their molar parts can be 7.6-11 parts, 9.55-11 parts, 10-11 parts, 10.5-11 parts, etc.

[0028] In some embodiments, the molar fraction of Ce is 0.2-0.37 parts, 0.2-0.35 parts, 0.2-0.33 parts, 0.2-0.3 parts, 0.2-0.27 parts, 0.2-0.25 parts, 0.2-0.23 parts, 0.2-0.21 parts, etc. The composition of the strong broadband absorbing glass also includes a clarifying agent, Ce, which is added in the form of cerium oxide. Cerium oxide has the advantage of improving the near-ultraviolet absorption capacity of the glass and is generally used in conjunction with nitrates. Cerium oxide decomposes at the melting temperature to release oxygen, effectively improving the internal quality and compositional homogeneity of the glass.

[0029] By controlling the content of elements such as Si, B, Al, Ca, and Ti that affect the coefficient of thermal expansion of glass, a glass with a coefficient of thermal expansion of (73-79)×10⁻⁶ at 30℃-300℃ was prepared. -7 A strong broad-spectrum absorption glass with a glass transition temperature of / ℃ was obtained. Furthermore, it significantly suppressed component volatilization loss, phase separation, and crystallization during high-temperature melting and drawing processes, resulting in a glass transition temperature T0. g 550℃, sag temperature T s 645 ℃, softening point T during wire drawing sp High-performance, broad-spectrum absorbing glass with a temperature of 740 °C.

[0030] By controlling the content of Co and Ni, glass can exhibit excellent light absorption in the 400-800 nm visible light band. By controlling the content of Cu and Cr, glass can exhibit excellent light absorption in the 350 nm-400 nm and 800-1000 nm bands. By controlling the total content of coloring elements such as Co, Ni, Cu, and Cr, glass can achieve good light absorption performance in the 350-1000 nm band.

[0031] By controlling the content of elements such as Si, B, Al, Ca, and Ti, glass can possess good chemical stability, high-temperature stability, and mechanical strength. However, if the glass composition, due to certain reasons (such as structural defects or the presence of a large number of highly polarizable elements), fails to maintain a stable state at high temperatures, it can create rapid ion diffusion channels. This causes the composition of the light-absorbing glass and adjacent optical fibers to deviate from the designed ratio, resulting in decreased optical uniformity and severely affecting the imaging sharpness and contrast of optical components. By controlling the content of elements such as Si, B, Al, Ca, and Ti, the diffusion rate and diffusion distance of ions can be significantly reduced.

[0032] Secondly, the present invention provides a method for preparing the aforementioned strong broad-spectrum absorption glass, comprising the following steps: After mixing the components of the glass material in the specified proportions, add the clarifying agent in the specified proportions and mix well. The mixture is melted at 1400-1500℃ and stirred at a speed of 10-15 r / min for 3-6 h. Mechanical stirring can accelerate the homogenization process of molten glass. Stirring continuously breaks down uneven areas and coarse streaks within the molten glass into very fine and short streaks, increasing the contact area and facilitating mutual dissolution and diffusion between the molten glass and the streaks, thus gradually eliminating or reducing the streaks. Ions with higher charges are relatively more difficult to diffuse. The introduction of nitrate oxidizing raw materials and melting in an air atmosphere can increase the valence state of cations, significantly reducing the diffusion rate and distance of ions.

[0033] Then, after high-temperature clarification and molding, glass products are obtained.

[0034] In some embodiments, the melting time is 8-12 hours. This melting time helps to clarify the molten glass.

[0035] In some embodiments, the molding temperature is 1300-1400℃ and the molding time is 7-12 min, thereby reducing the generation of secondary bubbles and impurities by shortening the molding time.

[0036] Thirdly, the present invention provides an application of the above-mentioned strong broad-spectrum absorbing glass in the preparation of light-absorbing glass fibers.

[0037] The beneficial effects of this invention are as follows: The glass material provided by this invention possesses optimized broad-spectrum absorption characteristics and high-temperature component stability, achieving a synergistic effect of high optical absorptivity and low component diffusion capability. Furthermore, the chemical composition of this material ensures excellent stability and processing performance under a wide range of environmental conditions, facilitating cutting, shaping, heat treatment, and wire drawing during manufacturing. Therefore, the glass material of this invention provides the necessary broad-spectrum absorption performance without sacrificing material reliability and processing ease, making it suitable for imaging elements requiring high image clarity and contrast.

[0038] The strong broadband absorption glass provided by this invention has a maximum transmittance of ≤1.3% in the visible light wavelength range of 500-700nm and a maximum transmittance of ≤26.8% in the wavelength range of 350-1000nm at a thickness of 0.5 mm. This indicates that the glass material of this invention has excellent absorption in a wide spectral range, ensuring the effectiveness of crosstalk absorption.

[0039] The strong broadband absorption glass provided by this invention has a maximum ion diffusion rate of 0.1-0.2 μm / h at 800 °C, a maximum ion diffusion distance ranging from 0.52 to 1.1 μm, and a coefficient of thermal expansion of (73-79)×10⁻⁶ at 30 °C-300 °C. -7 / ℃, glass transition temperature T g 550℃, sag temperature T s 645 ℃, softening point T during wire drawing sp 740 ℃. The glass achieves Class I acid resistance and Class I moisture resistance. It also possesses good high-temperature resistance and mechanical strength, making it suitable for image transmission elements requiring high image clarity and contrast.

[0040] Existing light-absorbing glasses have low average light absorption capacity in a wide wavelength range of 350-1000nm and poor high-temperature component stability. This invention prepares a strong broadband absorbing glass with excellent high-temperature component stability and high chemical stability by selecting and adjusting the types and ratios of glass raw materials and colorants. Attached Figure Description

[0041] The accompanying drawings, which form part of this invention, are used to provide a further understanding of the invention. The illustrative embodiments of the invention and their descriptions are used to explain the invention and do not constitute an improper limitation of the invention.

[0042] Figure 1 This is a comparison chart of the transmittance of Comparative Example 1 and Example 2 in the range of 350-1000nm. Detailed Implementation

[0043] To enable those skilled in the art to better understand the technical solution of the present invention, the technical solution of the present invention will be described in detail below with reference to specific embodiments and comparative examples.

[0044] Example 1 The composition of the strong broadband absorbing glass in this embodiment, the molar fraction of each component, and the physical properties of the glass are shown in Table 1.

[0045] The preparation method of strong broadband absorption glass is as follows: using quartz sand, boric acid, aluminum hydroxide, sodium nitrate, potassium carbonate, calcium carbonate, titanium oxide, manganese dioxide, cobalt oxide, nickel oxide, copper oxide, potassium dichromate and iron oxide as raw materials, adding cerium oxide as a clarifying agent, mixing thoroughly, melting at 1400℃ for 8 h, mechanically stirring (10 r / min, 3 h), and molding at 1300℃ (forming time is 7 min) to obtain glass rod material.

[0046] Transmittance was tested using a UV-Vis-IR spectrophotometer.

[0047] The coefficient of thermal expansion of glass samples was tested using a Netzsch DIL 402 thermal expansion meter. Sample preparation: The glass sample was polished into a cylindrical glass strip with a diameter of 6 × 50 mm, and both ends were made parallel. The heating rate was set to 5 °C / min, and the data acquisition period was 20 ms. The data were plotted as a temperature versus linear expansion curve, and the glass transition temperature and sag temperature were obtained using the tangent method. (GB / T 7962.16~2010) The softening point of the glass sample was tested using a plate viscometer. The sample was processed into a cylindrical glass strip with a diameter of 6×6 mm and parallel end faces.

[0048] The maximum ion diffusion distance and maximum ion diffusion rate of the glass were tested using a pellet method. K9 glass and light-absorbing glass were cut using an internal circular cutter to obtain 20 mm × 20 mm × 0.5 mm thin sheets. Both ends of the sheets were flat-ground and polished to a thickness of 0.3 mm for both the glass and light-absorbing sheets. Finally, the polished surfaces of the glass and light-absorbing sheets were aligned and placed in a hot-press mold, which was then weighed 5.0 kg and placed in an annealing furnace at 800℃. A HITACHI S-3500N X-ray scanning electron microscope (SEM) paired with an Oxford INCA energy dispersive spectrometer was used to scan the energy dispersive spectral lines of the natural cross-section of the pellet sample to obtain the concentration distribution of each element along the line. Elemental analysis at various points along the line yielded diffusion trend lines at the interface for each element. The distance from the point where the element concentration began to decrease to the point where the concentration stabilized was measured, thus determining the ion diffusion distance of each element. The diffusion rate of elements on the natural cross section of a light-absorbing glass slide at 800℃ was tested using a multifunctional in-situ variable temperature environment scanning electron microscope.

[0049] The acid resistance stability test of glass was conducted by Chengdu Guangming Optoelectronic Co., Ltd. Polished glass samples were eroded by test media with acidities of pH 2.9, pH 4.6, and pH 6.0. The time it took for the glass surface to exhibit violet-blue interference colors, surface discoloration, or peeling under incandescent light was observed. Based on the duration of this time, the acid resistance stability of colorless optical glass was classified in descending order. (GB / T 7962.14~2010) The moisture resistance stability test of the glass was conducted by Chengdu Guangming Optoelectronics Co., Ltd. The turbidity H0 and H1 of the tested sample and standard samples (BaK7 glass and ZK9 glass) before and after etching were measured respectively. The turbidity value H was calculated using H = H1 - H0. Based on the comparison with the turbidity value of the standard sample, the moisture resistance stability grade of the optical glass was obtained from a table. (GB / T 7962.15~2010) Example 2 The composition of the strong broadband absorbing glass in this embodiment, the molar fraction of each component, and the physical properties of the glass are shown in Table 1.

[0050] In the preparation method of the strong broadband absorption glass, the melting temperature is 1500℃ and the melting time is 12 h; mechanical stirring (15 r / min, 6 h), the forming temperature is 1400℃ and the forming time is 12 min, and other preparation steps, parameters and testing procedures are the same as in Example 1.

[0051] Example 3 The composition of the strong broadband absorption glass, the molar fraction of each component, and the physical properties of the glass are shown in Table 1.

[0052] In this embodiment, the preparation method of the strong broadband absorption glass is as follows: the melting temperature is 1460℃ and the melting time is 9h; mechanical stirring (12 r / min, 5 h) is used; the forming temperature is 1370℃ and the forming time is 10 min; other preparation steps, parameters and testing processes are the same as in Example 1.

[0053] Example 4 The composition of the strong broadband absorption glass, the molar fraction of each component, and the physical properties of the glass are shown in Table 1.

[0054] In this embodiment, the preparation method of the strong broadband absorption glass is as follows: the melting temperature is 1430℃ and the melting time is 9h; mechanical stirring (11 r / min, 4h) is used; the forming temperature is 1350℃ and the forming time is 8min; other preparation steps, parameters and testing processes are the same as in Example 1.

[0055] Example 5 The composition of the strong broadband absorption glass, the molar fraction of each component, and the physical properties of the glass are shown in Table 1.

[0056] In this embodiment, the preparation method of the strong broadband absorption glass is as follows: the melting temperature is 1480℃ and the melting time is 11h; mechanical stirring (13 r / min, 5 h) is used; the forming temperature is 1380℃ and the forming time is 11 min; other preparation steps, parameters and testing processes are the same as in Example 1.

[0057] Example 6 The composition of the strong broadband absorption glass, the molar fraction of each component, and the physical properties of the glass are shown in Table 1.

[0058] In this embodiment, the preparation method of the strong broadband absorption glass is as follows: the melting temperature is 1420℃ and the melting time is 8h; mechanical stirring (11 r / min, 4h) is used; the forming temperature is 1340℃ and the forming time is 9min; other preparation steps, parameters and testing processes are the same as in Example 1.

[0059] Comparative Examples 1-5 The composition of the glass materials and the physical properties of the glass obtained in Comparative Examples 1-5 are shown in Table 2. The introduction of each component, the glass preparation steps, parameters and testing procedures are the same as in Example 1.

[0060] Table 1. Composition and physical properties of the glass in Examples 1-6 of the present invention

[0061] Table 2. Composition and physical properties of light-absorbing glasses in Comparative Examples 1-5

[0062] Examples 1-6, by rationally adding appropriate components and controlling the proportions of each component in the raw materials, achieve better high-temperature component stability of the glass while ensuring excellent broad-spectrum absorption performance. As shown in Table 1, the optical transmittance of the strong broad-spectrum absorption glass prepared from the glass components of Examples 1-6 of this invention is as follows: in the 500-700 nm range, the maximum transmittance is ≤1.3%; in the 350-1000 nm range, the maximum transmittance is ≤26.8%. The overall performance is superior to that of Comparative Examples 1-2 and the glass involved in the prior art.

[0063] Figure 1 This is a comparison chart of the transmittance of Comparative Example 2 and Example 2 in the range of 350-1000nm.

[0064] As can be seen from the above, the strong broadband absorption glass provided in Examples 1-6 of the present invention possesses excellent broadband absorption performance and good high-temperature component stability, while also exhibiting good high-temperature resistance and chemical stability. This is because Examples 1-6 of the present invention incorporate Co, Ni, Cu, and Cr in the preparation of the strong broadband absorption glass, and also maintain the content and proportion of some components in the raw materials, while setting appropriate melting and forming temperatures and stirring processes. Therefore, the strong broadband absorption glass of the present invention has excellent broadband absorption performance and good high-temperature component stability, and has great potential for application in fiber optic imaging elements that require high imaging clarity and contrast.

[0065] The above description is merely a preferred embodiment of the present invention and is not intended to limit the invention. Various modifications and variations can be made to the present invention by those skilled in the art. Any modifications, equivalent substitutions, improvements, etc., made within the spirit and principles of the present invention should be included within the scope of protection of the present invention.

Claims

1. A strong broadband absorbing glass, characterized in that, The molar count includes the following elements: The composition is as follows: Si 12-15 parts, B 6-8 parts, Al 0.5-1 parts, Na 6-8 parts, K 5-8 parts, Ca 2-3 parts, Ti 1-2 parts, Fe 1-2 parts, Co 4-6 parts, Ni 1-2.5 parts, Mn 0-0.1 parts, Cu 0.2-0.5 parts, Cr 0.3-1 parts, Ce 0.2-0.4 parts; wherein the sum of the molar parts of Si, B, Al, Ca and Ti is 24-26.5 parts.

2. The strong broadband absorption glass as described in claim 1, characterized in that, The molar fractions of Si are 12.1-15 parts, 12.3-15 parts, 12.7-15 parts, 13-15 parts, 13.3-15 parts, 13.5-15 parts, 13.7-15 parts, 14-15 parts, 14.3-15 parts, 14.5-15 parts, or 14.7-15 parts; Alternatively, the molar amounts of B are 6.3-8 parts, 6.7-8 parts, 6.9-8 parts, 7-8 parts, 7.3-8 parts, 7.5-8 parts, and 7.7-8 parts; Alternatively, the molar amounts of Al are 0.5-0.9 parts, 0.5-0.8 parts, 0.5-0.7 parts, and 0.5-0.6 parts; Alternatively, the molar amounts of Na are 6-7.7 parts, 6-7.5 parts, 6-7.3 parts, 6-7 parts, 6-6.7 parts, 6-6.5 parts, or 6-6.3 parts; Alternatively, the molar amounts of K are 5-7.7 parts, 5-7.5 parts, 5-7.3 parts, 5-7 parts, 5-6.7 parts, 5-6.5 parts, 6.1-6.5 parts, 6.1-7.7 parts, 6.1-7.5 parts, 6.1-7.3 parts, 6.1-7 parts, and 6.1-6.7 parts; Alternatively, the molar amounts of Ca are 2-2.9 parts, 2-2.6 parts, 2-2.4 parts, 2-2.2 parts, and 2-2.1 parts; Alternatively, the molar amounts of Ti are 1-1.9 parts, 1-1.7 parts, 1-1.4 parts, 1-1.2 parts, or 1-1.1 parts; Alternatively, the molar amounts of Co are 4.3-6 parts, 4.5-6 parts, 4.7-6 parts, 5-6 parts, 5.3-6 parts, 5.5-6 parts, 5.7-6 parts, and 5.9-6 parts; Alternatively, the molar amounts of Ni are 1.1-2.5 parts, 1.3-2.5 parts, 1.5-2.5 parts, 1.7-2.5 parts, 2-2.5 parts, or 2.3-2.5 parts; Alternatively, the molar amounts of Cu are 0.2-0.45 parts, 0.2-0.4 parts, 0.2-0.35 parts, 0.2-0.3 parts, 0.2-0.27 parts, 0.2-0.25 parts, and 0.2-0.22 parts; Alternatively, the molar amounts of Cr are 0.3-0.9 parts, 0.3-0.7 parts, 0.3-0.5 parts, and 0.3-0.4 parts; Alternatively, the molar fractions of Fe are 1.1-2 parts, 1.3-2 parts, 1.5-2 parts, 1.7-2 parts, and 1.9-2 parts; Alternatively, the molar amounts of Mn are 0.01-0.1 parts, 0.01-0.09 parts, 0.01-0.07 parts, 0.01-0.05 parts, and 0.01-0.03 parts; Alternatively, the molar amounts of Ce are 0.2-0.37 parts, 0.2-0.35 parts, 0.2-0.33 parts, 0.2-0.3 parts, 0.2-0.27 parts, 0.2-0.25 parts, 0.2-0.23 parts, and 0.2-0.21 parts.

3. The strong broad-spectrum absorption glass as described in claim 1, characterized in that Na... The sum of the molar amounts of K and K is no more than 15 parts; preferably 12-15 parts, 12-14 parts, or 12-13 parts.

4. The strong broadband absorption glass as described in claim 1, characterized in that, The sum of the molar parts of Si, B, Al, Ca and Ti is 25-26.5 parts or 26-26.5 parts.

5. The strong broadband absorption glass as described in claim 1, characterized in that, The sum of the molar parts of Co and Ni is 5-8.5, 6-8.5, 7-8.5, or 8-8.5 parts; Alternatively, the sum of the molar parts of Cu and Cr is 0.5-1.5 parts, 0.5-1.1 parts, 0.5-1 parts, or 0.5-0.9 parts.

6. The strong broadband absorption glass as described in claim 1, characterized in that, The sum of the molar parts of Co, Ni, Cu, Cr, Fe and Mn is not less than 7.6 parts; preferably, the sum of the molar parts is 7.6-11 parts, 9.55-11 parts, 10-11 parts or 10.5-11 parts.

7. A method for preparing a strong broad-spectrum absorbing glass according to any one of claims 1 to 6, characterized in that, Includes the following steps: After mixing the components of the glass material in the specified proportions, add the clarifying agent in the specified proportions and mix well. The mixture is melted at 1400-1500℃ and stirred at a speed of 10-15 r / min for 3-6 h. Then, after high-temperature clarification and molding, glass products are obtained.

8. The preparation method according to claim 7, characterized in that, The melting time is 8-12 hours.

9. The preparation method according to claim 7, characterized in that, The molding temperature is 1300-1400℃, and the molding time is 7-12 min.

10. The application of the strong broad-spectrum absorbing glass according to any one of claims 1 to 6 in the preparation of light-absorbing glass fibers.

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