A method for preparing high-strength and high-modulus inorganic mineral fiber using water-quenched slag

Abstract

The present invention belongs to the technical field of inorganic mineral fiber preparation and provides a method for preparing high-strength and high-modulus inorganic mineral fiber using water-quenched slag. First, the chemical purity of the raw materials is improved through density separation and pickling. At the same time, the addition of Na2CO3 and Fe2O3 reduces the tendency of crystal precipitation and improves the vitrification characteristics of the water-quenched slag. Secondly, the composite oxide modifier further optimizes the structure of the glass network. B2O3 enhances the chemical stability of the glass network and reduces the melt viscosity by forming B-O-Si bonds. Y2O3 provides a high electric field strength, inhibits crystal precipitation and enhances the crosslinking degree of the network. V2O5 provides a redox buffer function through its variable valence state, optimizes the chemical environment of the melting process and improves creep resistance. Finally, a dense Al2O3 coating is formed on the fiber surface, improving the mechanical strength, oxidation resistance, corrosion resistance and high-temperature stability of the fiber.

Description

Technical Field

[0001] The invention belongs to the technical field of inorganic mineral fiber preparation, and relates to a method for preparing high-strength and high-modulus inorganic mineral fiber by utilizing water-quenched slag. Background Art

[0002] Quenched slag is an important solid waste generated during the metallurgical production process. It is a special material formed by the rapid cooling of high-temperature molten slag after metal smelting. Its production process mainly originates from steel smelting. By rapidly contacting the high-temperature molten slag with a large amount of cold water, it is rapidly cooled and solidified to form an amorphous glassy solid material. The chemical composition of water-quenched slag is complex, mainly including silicon dioxide, calcium oxide, aluminum oxide, magnesium oxide and other trace oxides. This material has an amorphous structure. Due to the rapid cooling to form a glassy solid, it has a large surface area, high chemical activity, and a uniform microstructure. Water-quenched slag has important resource value in industrial production and can be widely used in cement production, civil engineering, roadbed materials and other fields. Its unique chemical composition and physical structure make it a highly promising industrial by-product.

[0003] However, the main problem in the process of preparing water-quenched slag into inorganic mineral fibers is that during the high-temperature heat treatment stage, the components in the water-quenched slag are very prone to crystallization. This crystallization phenomenon will seriously affect the microstructure of the fiber, causing a large number of crystal nuclei to form inside the fiber, significantly reducing the overall strength of the fiber. Crystallization not only makes the internal structure of the fiber uneven, but also forms stress concentration areas in the fiber, fundamentally weakening the mechanical properties of the fiber, making it difficult to meet the technical requirements of high strength and high modulus. Therefore, it is necessary to inhibit crystallization during the preparation of water-quenched slag, maintain the amorphous structure of the fiber, and improve the performance of inorganic mineral fibers. Summary of the Invention

[0004] In view of the shortcomings of the existing technology, the purpose of the present invention is to provide a high-strength and high-modulus inorganic mineral fiber prepared by using water-quenched slag and a preparation method thereof. By density separation, acid washing purification and high-temperature calcination of the water-quenched slag, fluxes Na2CO3 and Fe2O3 are introduced to optimize its chemical composition and improve its vitrification ability. The composite modification system composed of B2O3, Y2O3 and V2O5 improves the uniformity, chemical stability and processing performance of the melt by enhancing network crosslinking, inhibiting crystal precipitation and redox buffering, respectively. A dense Al2O3 coating is deposited and calcined on the fiber surface, which significantly improves the fiber's high temperature resistance, chemical corrosion resistance and matrix interface bonding performance, thereby meeting the needs of actual production.

[0005] To achieve this object, the present invention adopts the following technical solutions:

[0006] In a first aspect, the present invention provides a method for preparing high-strength and high-modulus inorganic mineral fibers using water-quenched slag, the preparation method comprising:

[0007] Step S1: placing the water-quenched slag raw material into a vibrating screen for particle classification, retaining a medium-sized particle portion, pouring the water-quenched slag of the medium-sized particle portion into a lithium chloride solution, collecting the floated portion, filtering and washing it, and then fully drying it at a first temperature; placing the dried floated water-quenched slag into a hydrochloric acid solution, fully stirring it at room temperature, filtering and washing it, and then fully drying it at the first temperature to obtain acid-washed water-quenched slag particles; crushing the acid-washed water-quenched slag particles to below a target particle size, and then mixing them with Na2CO3 and Fe2O3, heating them to a second temperature and continuously calcining them, and cooling them to room temperature after the calcination to obtain high-temperature sintered water-quenched slag;

[0008] Step S2, mixing a boric acid solution with an yttrium nitrate solution to obtain a mixed solution, dissolving vanadium pentoxide in ammonia water and adding the solution to the mixed solution, stirring evenly, adjusting the pH to 8-8.5 with ammonia water, maintaining stirring to complete the precipitation reaction, filtering and washing, and drying at a third temperature to obtain a wet powder precursor, then mixing H3BO3, Y2O3 and V2O5 to obtain a mixture, the mixture and the wet powder precursor are put into a ball mill together, and ethanol is added. After ball milling, the mixture is calcined at a second temperature to obtain a composite oxide modifier;

[0009] Step S3: mixing the high-temperature sintered water-quenched slag, the composite oxide modifier, and borax, ball-milling the mixture to obtain a mixed material, heating the mixed material to a fourth temperature, drawing the molten material into fibers using a fiber blowing device, and then placing the fibers in an argon atmosphere and annealing them at a fifth temperature to obtain annealed fibers;

[0010] Step S4, immersing the annealed fiber in anhydrous ethanol, ultrasonically cleaning to remove surface contaminants and then drying at a first temperature, dissolving aluminum nitrate in deionized water, stirring until dissolved, and then adding an ammonia solution to adjust the pH to 7.5 to obtain an Al(OH)3 suspension, immersing the dried annealed fiber in the Al(OH)3 suspension, keeping it for a certain period of time, then taking out the annealed fiber, and calcining it at a second temperature to obtain a high-strength and high-modulus inorganic mineral fiber prepared using water-quenched slag.

[0011] Water-quenched slag is a complex solid waste, typically composed of various silicates, aluminosilicates, oxides, and minor metal elements. Its main components include: an amorphous silicate glass phase, such as the SiO₂-Al₂O₃-CaO system; crystalline impurities, such as calcium oxide (CaO), magnesium oxide (MgO), and unreduced metallic iron (Fe); and unreacted light components, such as porous amorphous materials or low-density glassy particles. When water-quenched slag is placed in a lithium chloride solution, lower-density particles (such as those containing amorphous light silicates) float to the surface, while higher-density particles (such as metal oxides and unreacted metals) sink to the bottom. High-density particles in water-quenched slag often contain metallic iron, which can lead to uneven melting during fiber preparation. High-density residues (such as unreacted metals or metal oxides) can introduce defects and reduce the mechanical properties of the fibers. The floating fraction is primarily composed of low-density amorphous silicate particles, the core raw material for fiber preparation. Amorphous silicate particles have a high glass-forming ability, allowing them to form uniform glassy fibers when melted at high temperatures. In contrast, the crystalline components in high-density impurities are more prone to crystallization at high temperatures, resulting in the appearance of grain boundaries inside the material, reducing the strength and modulus of the fiber. The flotation process removes high-density impurities. If these high-density particles are not separated, non-uniform melts may be produced during the subsequent melting process, leading to non-uniform phases during the fiberization process; brittle impurities are introduced, forming stress concentration points, reducing the mechanical properties of the fiber; and the fiber surface becomes rough, affecting the final modulus and strength.

[0012] Amorphous silicates in water-quenched slag are materials that fail to form a crystalline structure upon rapid cooling. Their molecular structure consists of a disordered silicon-oxygen network, which possesses a high vitrification ability and serves as a core material for fiber preparation. The key properties of amorphous materials lie in their structural disorder and uniformity, which imparts excellent mechanical properties and thermal stability. However, crystalline impurities in water-quenched slag, such as CaO, MgO, and unreacted silicates, often exist as localized crystalline phases or weakly bound phases within the amorphous matrix. Their presence causes the material to form crystalline phases (such as CaSiO3) at high temperatures. These phases disrupt the glassy uniformity, thereby reducing the strength and modulus of the fiber. At high temperatures, these crystalline impurities react chemically with silicon oxide (SiO2) or aluminum silicates (Al2O3·SiO2) in the amorphous matrix, forming new crystalline phases. For example, the reaction between CaO and SiO2 forms calcium silicate crystals. CaO is an alkaline oxide that reacts with SiO2 in the amorphous silicate matrix under high temperature conditions to form CaSiO3 crystals. CaSiO3 is a crystallized phase whose crystal structure destroys the original continuous network structure. The reaction between MgO and SiO2 forms magnesium silicate crystals (MgSiO3), which also destroys the uniformity of the network. In the amorphous structure, atoms such as Si, O, and Al are arranged in a disordered manner to form a continuous silicon-oxygen network. Crystallized phases (such as CaSiO3 and MgSiO3) have a highly ordered crystal structure. The formation of these crystalline phases can lead to local phase separation in the matrix, that is, the formation of an interface between the crystalline phase and the amorphous matrix. The interface between the crystalline phase and the matrix cannot withstand high-intensity mechanical stress, reducing the strength of the material. The formation of the crystalline phase disrupts the continuity of the network, resulting in uneven stress distribution at the microscale. Furthermore, the thermal expansion coefficients of the crystalline phase and the amorphous matrix differ (for example, CaSiO3 has a higher thermal expansion coefficient than the amorphous silicate matrix), introducing thermal stresses during temperature changes. Grain boundaries are stress concentration points, and microcracks are prone to form and propagate under external forces, ultimately reducing the material's strength. At high temperatures, crystalline impurities chemically react with the amorphous matrix, generating a crystalline phase that disrupts the material's uniformity and introduces grain boundaries, leading to stress concentration and crack propagation paths within the material. The formation of the crystalline phase directly weakens the integrity of the network, reducing the material's strength and modulus.

[0013] One of the core elements of inorganic mineral fiber materials prepared from water-quenched slag is the silicon-oxygen network. Its molecular structure consists of silicon atoms connected to each other by covalent bonds through oxygen atoms, forming a three-dimensional network structure. The key feature of the structure is bridging oxygen. Bridging oxygen is an oxygen atom connecting two silicon atoms, which gives the glass network a high degree of crosslinking and mechanical strength. Non-bridging oxygen refers to an oxygen atom connected to only one silicon atom, and its other end is negatively charged. The presence of non-bridging oxygen reduces the rigidity and uniformity of the network. The introduction of alkaline oxides will destroy the continuity of the silicon-oxygen network. At high temperatures, CaO and MgO will dissociate into CaO. 2+ Mg 2+ ions and O 2- ions, O 2- Ions react with the bridging oxygen in the silicon-oxygen network. Bridging oxygen is a symmetrical covalent bond structure, O 2- Due to its high electronegativity and strong electron affinity, ions tend to compete with oxygen atoms for the bonding ability of silicon atoms. 2- When it is close to the bridging oxygen, the strong electron affinity leads to polarization of the bridging oxygen bond. 2- The introduction of causes the Si-O-Si bond to break, and the oxygen atoms are transformed from the bridging oxygen state to two independent non-bridging oxygens. The cross-linking degree in the silicon-oxygen network is reduced, resulting in a decrease in the mechanical properties of the material. At the same time, the uniformity of the material is destroyed. At the same time, the reduction of bridging oxygen will reduce the rigidity of the network, causing the glass transition temperature and softening point of the material to drop significantly, reducing the thermal stability of the material. After CaO and MgO are dissolved in hydrochloric acid, the number of non-bridging oxygen in the silicon-oxygen network is reduced, the cross-linking degree is increased, and the rigidity and strength of the material are enhanced. At the same time, the removal of alkaline oxides and weakly bound phases at the boundaries reduces the tendency of calcium silicate and magnesium silicate crystals to form during high-temperature melting, making the melt more inclined to form an amorphous structure rather than precipitate crystals when cooling. The removal of weakly bound phases and crystalline phases reduces stress concentration points inside the material, reduces the risk of crack initiation and expansion, and thus improves the mechanical properties of the fiber.

[0014] In the borate system, boron atoms form covalent bonds with oxygen atoms to form two basic structural units, BO3 (planar triangle) and BO4 (tetrahedron). The BO3 unit is the main structural form of borates, in which the boron atom is connected to three oxygen atoms through three BO bonds to form a planar triangle structure. The BO3 unit has high structural flexibility and can be embedded in the silicon-oxygen network to improve the fluidity of the water-quenched slag after high-temperature melting. When borates coexist with other oxides, the O in the oxides 2-Ions can react with BO3 units, converting part of BO3 into BO4 tetrahedral units. BO4 units have strong network bonding ability. During the melting process, the oxygen atoms of BO4 units are shared with the oxygen atoms of SiO4 units to generate Si-OB bonds. This bridge bond structure enhances the cross-linking degree of the network, improves the mechanical strength and chemical stability. When BO4 units replace part of the SiO4 units, the silicon-oxygen network is partially replaced by BO-Si or BOB bridge bonds, which can optimize the elasticity and viscosity of the network and help achieve low melting temperature and high fluidity. At the same time, in the borosilicate system, alkaline oxides will introduce additional O 2- , promoting the transformation of BO3 to BO4. The participation of alkaline oxides reduces the melting temperature while maintaining a certain network structure strength.

[0015] Y 3+ It is a rare earth metal ion with a small radius and a high charge density, so Y 3＋ Has a strong electrostatic attraction, making Y 3+ Ions easily react with O 2- Ion combination forms a stable oxide bond (YO bond), the bond energy of the YO bond is high, which makes the introduction of Y 3＋ Ions can improve the strength and stability of inorganic mineral fibers. In the material system, SiO2 and Al2O3 are the main network formers. The basic units are silicon oxide tetrahedron (SiO4) and aluminum oxide tetrahedron (AlO4). These tetrahedrons are connected by bridging oxygen (Si-O-Si or Si-O-Al) to form a network. After the introduction of Y2O3, Y 3+ Ions can react with O 2- ions form a strong YO bond, Y 3+ The ions are connected to SiO4 or AlO4 units through bridging oxygen to form Si-OY or Al-OY bonds. These newly formed bridge bonds increase the degree of cross-linking, thereby enhancing the strength of the material. 3+ Ions can neutralize the negative charge of AlO4 units, further improving the stability of the material. The introduction of Y2O3 can also inhibit the crystal precipitation in the fiber. In the water-quenched slag melt, the ions in the local area (such as Ca 2+ Mg 2+ ) Through diffusion and rearrangement, a crystal nucleus with a periodic structure is formed. The crystal nucleus continuously absorbs the surrounding ions to form a long-range ordered crystal structure. The introduction of Y2O3 into the water-quenched slag melt can interfere with the diffusion of ions or destroy their orderly arrangement, and the probability of crystal nucleation will be greatly reduced. Even if a crystal nucleus is formed, these interferences will prevent the further growth of the crystal nucleus, thereby inhibiting crystal precipitation. 3+ Ions have a high charge density, and their strong electrostatic effect can significantly affect the distribution of surrounding ions and change the Ca 2+ and Mg2+ The migration path of plasma in the melt makes it difficult for these ions to arrange themselves in the periodic pattern required by the crystal. 3+ Ions can combine with SiO4 or AlO4 units in the glass network to form Si-OY or Al-OY bonds, which will introduce disorder in local areas and destroy the chemical symmetry and uniformity required for crystal formation; at the same time, Y 3+ The high electric field strength of the ions enables them to preferentially react with O 2- coordination, especially in the melt, Y 3+ The affinity for oxygen is much higher than that for Ca 2+ and Mg 2+ , when Y 3+ Ions and O 2- When combined to form a YO bond, Ca 2+ and Mg 2+ are repelled to other areas of the melt, resulting in uneven distribution of ion concentrations required for crystal growth, and the probability of nucleation formation is greatly reduced; and in the melt, Ca 2+ and Mg 2+ Plasma needs to diffuse with O 2- Combined with SiO4 and other units, it eventually forms a crystal structure, Y 3+ The introduction of Ca leads to the enhancement of the Coulomb interaction between ions in the melt. 2+ and Mg 2+ The increase in energy required for migration makes it difficult for ions to arrange in the direction of crystal growth in the melt. Crystal precipitation usually reduces the high-temperature performance of the material. The introduction of Y2O3 inhibits crystal precipitation, making the fiber exhibit better thermal stability and strength at high temperatures.

[0016] V2O5 is an oxide that is very easy to melt. It acts as a strong flux in the system and can significantly reduce the melting temperature of water-quenched slag. After V2O5 is introduced, it can interact with SiO2 and Al2O3 to break some silicon-oxygen bonds, thereby reducing the viscosity of the melt. The reduction in melting temperature reduces energy consumption in the fiber preparation process, improves production efficiency, improves the fluidity of the melt, and reduces broken or uneven wires. The vanadium in V2O5 can exhibit two main oxidation states in the molten material: V 5+ and V 4+ , which makes it have redox buffer function, in an oxidizing atmosphere V 4+ Oxidized to V 5+ , forming V2O5, under reducing atmosphere V 5+ Partially restored to V 4+ , forming V-containing 4+ Vanadium oxides (such as VO2 +), during the glass melting process, fluctuations in redox conditions may lead to uneven distribution or precipitation of certain components. This redox balance allows the chemical environment of the melt to be dynamically adjusted, improving the uniformity of the fiber. At the same time, the redox properties of V2O5 enable it to capture oxygen free radicals generated in the glass melt, effectively inhibiting the occurrence of free radical chain reactions. 5+ By restoring to V 4+ It absorbs some free electrons, reduces the concentration of free radicals, reduces the component separation and phase separation caused by free radicals in the melt, and improves the chemical uniformity of the material. 3+ The high electric field strength and V 5+ / V 4+ Combined with the redox ability of Y2O3, it can further enhance the chemical stability of the glass by forming a stable YOV bond with V2O5. The introduction of V2O5 significantly increases the structural rigidity of the glass network by forming strong VO-Si, VOB and VOY bonds. The addition of B2O3 further improves the high-temperature toughness of the glass, while the high thermal stability of Y2O3 enhances the overall support of the fiber at high temperatures, making the fiber exhibit a lower creep rate in high-temperature environments.

[0017] B2O3 exists in the melt in the form of BO3 or BO4 units. Its introduction can enhance the chemical stability of the fiber and reduce the viscosity of the melt. BO3 and BO4 units can synergize with SiO4 units to form a more stable borosilicate network, thereby improving the uniformity and mechanical properties of the fiber; Y2O3 forms YO-Si or YOB bonds with SiO4 or BO3 units to enhance the degree of crosslinking. 3+ The high electric field strength of the ions inhibits crystal precipitation during melting, ensuring the melt maintains an amorphous structure during cooling. The variable valence of V2O5 provides a redox buffer during melting, dynamically adjusting the chemical environment of the glass, inhibiting crystal formation, and optimizing the melt's fluidity. At high temperatures, the mixed materials melt to form a uniform glassy melt. During fiber drawing, the melt is drawn into fibers through a fiber blowing device. Strong bonds (Si-O, BO, YO, and VO bonds) provide the fibers' mechanical strength. The composite oxide modifier allows rapid cooling at high temperatures, solidifying the glass melt into an amorphous structure and preventing crystal precipitation, thereby ensuring fiber uniformity and toughness. The annealing process slowly releases residual stress in the fiber, eliminating localized internal stresses generated during the drawing process, resulting in fibers with increased mechanical strength and thermal stability.

[0018] The surface of the fiber is rich in silicon-oxygen networks. Some silicon-oxygen bonds on the fiber surface will be hydrolyzed by water to generate active hydroxyl groups. Hydroxyl groups are hydrophilic and chemically active, which are the main adsorbents of Al. 3+ The key site of the ion, hydroxyl group can3+ The ions react to form strong chemical bonds, which enhance the bonding force between the deposited layer and the fiber matrix, thereby improving the adhesion and stability of the coating. In addition, the dissolved Al 3+ ions and OH - Ionic bonding forms aluminum hydroxide precipitates, and the Al(OH)3 precipitate is in a colloidal state and easily adsorbed on the fiber surface, resulting in good bonding between the coating and the substrate interface. The calcination process dehydrates and decomposes the deposited Al(OH)3, converting it into a dense alumina coating. High-temperature calcination densifies the Al2O3 coating on the fiber surface while retaining the strong bonding formed by chemical bonding, further enhancing the bonding between the coating and the fiber substrate. The calcined Al2O3 coating is a high-hardness, high-strength inorganic material that enhances the fiber's tensile strength and wear resistance, while also improving the fiber's resistance to acid and alkali corrosion.

[0019] As a preferred technical solution of the present invention, in step S1, the particle size of the medium particle part is 100-1000 μm.

[0020] In some optional examples, the density of the lithium chloride solution is 1.3 g / cm 3 .

[0021] In some optional examples, the mass ratio of the medium particle portion to the lithium chloride solution is 1:(5-6), for example, it can be 1:5.0, 1:5.1, 1:5.2, 1:5.3, 1:5.4, 1:5.5, 1:5.6, 1:5.7, 1:5.8, 1:5.9 or 1:6.0, but is not limited to the listed values, and other unlisted values ​​within the numerical range are also applicable.

[0022] In some optional examples, the first temperature is 120-130°C, for example, it can be 120.0°C, 121.0°C, 122.0°C, 123.0°C, 124.0°C, 125.0°C, 126.0°C, 127.0°C, 128.0°C, 129.0°C or 130.0°C, but is not limited to the listed values, and other unlisted values ​​within the numerical range are also applicable.

[0023] In some optional examples, the drying time of the floated part is 12-14h, for example, it can be 12.0h, 12.2h, 12.4h, 12.6h, 12.8h, 13.0h, 13.2h, 13.4h, 13.6h, 13.8h or 14.0h, but is not limited to the listed values, and other unlisted values ​​within the numerical range are also applicable.

[0024] In some optional examples, the mass fraction of the hydrochloric acid solution is 3-4wt.%, for example, it can be 3.0wt.%, 3.1wt.%, 3.2wt.%, 3.3wt.%, 3.4wt.%, 3.5wt.%, 3.6wt.%, 3.7wt.%, 3.8wt.%, 3.9wt.% or 4.0wt.%, but is not limited to the listed values, and other unlisted values ​​within this numerical range are also applicable.

[0025] In some optional examples, the solid-liquid ratio of the floated portion to the hydrochloric acid solution is 1 g:10 mL.

[0026] In some optional examples, the stirring time at room temperature is 2-3h, for example, it can be 2.0h, 2.1h, 2.2h, 2.3h, 2.4h, 2.5h, 2.6h, 2.7h, 2.8h, 2.9h or 3.0h, but is not limited to the listed values, and other unlisted values ​​within the numerical range are also applicable.

[0027] In some optional examples, the drying time after stirring with hydrochloric acid is 12-14 hours, for example, it can be 12.0 hours, 12.2 hours, 12.4 hours, 12.6 hours, 12.8 hours, 13.0 hours, 13.2 hours, 13.4 hours, 13.6 hours, 13.8 hours or 14.0 hours, but is not limited to the listed values, and other unlisted values ​​within the numerical range are also applicable.

[0028] In some optional examples, the target particle size is 50 μm.

[0029] In some optional examples, the mass of the Na2CO3 is 5-10% of the mass of the pickling water-quenched slag particles, for example, it can be 5.0%, 5.5%, 6.0%, 6.5%, 7.0%, 7.5%, 8.0%, 8.5%, 9.0%, 9.5% or 10.0%, but is not limited to the listed values, and other unlisted values ​​within this numerical range are also applicable.

[0030] In some optional examples, the mass of the Fe2O3 is 2-4% of the mass of the pickling water-quenched slag particles, for example, it can be 2.0%, 2.2%, 2.4%, 2.6%, 2.8%, 3.0%, 3.2%, 3.4%, 3.6%, 3.8% or 4.0%, but is not limited to the listed values, and other unlisted values ​​within this numerical range are also applicable.

[0031] In some optional examples, the second temperature is 850-950°C, for example, it can be 850.0°C, 860.0°C, 870.0°C, 880.0°C, 890.0°C, 900.0°C, 910.0°C, 920.0°C, 930.0°C, 940.0°C or 950.0°C, but is not limited to the listed values, and other unlisted values ​​within the numerical range are also applicable.

[0032] In some optional examples, the second temperature calcination time is 2-3h, for example, it can be 2.0h, 2.1h, 2.2h, 2.3h, 2.4h, 2.5h, 2.6h, 2.7h, 2.8h, 2.9h or 3.0h, but is not limited to the listed values, and other unlisted values ​​within the numerical range are also applicable.

[0033] As a preferred technical solution of the present invention, in step S2, the mass ratio of boric acid to deionized water in the boric acid solution is 1:10.

[0034] In some optional examples, in the yttrium nitrate solution, the mass ratio of yttrium nitrate hexahydrate to deionized water is 4:25.

[0035] In some optional examples, the mass ratio of the vanadium pentoxide to ammonia water is 1:15.

[0036] In some optional examples, the mass fraction of the ammonia water is 20 wt.%.

[0037] In some optional examples, the mass ratio of the boric acid, yttrium nitrate hexahydrate, and vanadium pentoxide is 5:8:2.

[0038] In some optional examples, the stirring reaction time is 30-50 min, for example, it can be 30.0 min, 32.0 min, 34.0 min, 36.0 min, 38.0 min, 40.0 min, 42.0 min, 44.0 min, 46.0 min, 48.0 min or 50.0 min, but is not limited to the listed values, and other unlisted values ​​within the numerical range are also applicable.

[0039] In some optional examples, the third temperature is 80-100°C, for example, it can be 80.0°C, 82.0°C, 84.0°C, 86.0°C, 88.0°C, 90.0°C, 92.0°C, 94.0°C, 96.0°C, 98.0°C or 100.0°C, but is not limited to the listed values, and other unlisted values ​​within the numerical range are also applicable.

[0040] In some optional examples, the third temperature drying time is 10-12h, for example, it can be 10.0h, 10.2h, 10.4h, 10.6h, 10.8h, 11.0h, 11.2h, 11.4h, 11.6h, 11.8h or 12.0h, but is not limited to the listed values, and other unlisted values ​​within the numerical range are also applicable.

[0041] In some optional examples, the mass ratio of H3BO3, Y2O3, and V2O5 is 4:3:2.

[0042] In some optional examples, the mass ratio of the mixture to the wet powder precursor is 2:3.

[0043] In some optional examples, the ball milling time is 2-3h, for example, it can be 2.0h, 2.1h, 2.2h, 2.3h, 2.4h, 2.5h, 2.6h, 2.7h, 2.8h, 2.9h or 3.0h, but is not limited to the listed values, and other unlisted values ​​within the numerical range are also applicable.

[0044] In some optional examples, the calcination time is 4-6h, for example, it can be 4.0h, 4.2h, 4.4h, 4.6h, 4.8h, 5.0h, 5.2h, 5.4h, 5.6h, 5.8h or 6.0h, but is not limited to the listed values, and other unlisted values ​​within the numerical range are also applicable.

[0045] As a preferred technical solution of the present invention, in step S3, the mass ratio of the high-temperature sintered water-quenched slag, the composite oxide modifier and borax is (60-70): (20-30): (10-20).

[0046] In some optional examples, the ball milling time is 40-60 min, for example, it can be 40.0 min, 42.0 min, 44.0 min, 46.0 min, 48.0 min, 50.0 min, 52.0 min, 54.0 min, 56.0 min, 58.0 min or 60.0 min, but is not limited to the listed values, and other unlisted values ​​within the numerical range are also applicable.

[0047] In some optional instances, the fourth temperature is 1450-1550°C, for example, it can be 1450.0°C, 1460.0°C, 1470.0°C, 1480.0°C, 1490.0°C, 1500.0°C, 1510.0°C, 1520.0°C, 1530.0°C, 1540.0°C or 1550.0°C, but is not limited to the listed values, and other unlisted values ​​within the numerical range are also applicable.

[0048] In some optional instances, the fifth temperature is 400-500°C, for example, it can be 400.0°C, 410.0°C, 420.0°C, 430.0°C, 440.0°C, 450.0°C, 460.0°C, 470.0°C, 480.0°C, 490.0°C or 500.0°C, but is not limited to the listed values, and other unlisted values ​​within the numerical range are also applicable.

[0049] In some optional examples, the holding time of the annealing treatment is 60-80 min, for example, it can be 60.0 min, 62.0 min, 64.0 min, 66.0 min, 68.0 min, 70.0 min, 72.0 min, 74.0 min, 76.0 min, 78.0 min or 80.0 min, but is not limited to the listed values. Other unlisted values ​​within this numerical range are also applicable. The cooling rate is 3°C / min.

[0050] As a preferred technical solution of the present invention, in step S4, the ultrasonic cleaning time is 10-20 min, for example, it can be 10.0 min, 11.0 min, 12.0 min, 13.0 min, 14.0 min, 15.0 min, 16.0 min, 17.0 min, 18.0 min, 19.0 min or 20.0 min, but is not limited to the listed values, and other unlisted values ​​within the numerical range are also applicable.

[0051] In some optional examples, the drying time is 2-3h, for example, it can be 2.0h, 2.1h, 2.2h, 2.3h, 2.4h, 2.5h, 2.6h, 2.7h, 2.8h, 2.9h or 3.0h, but is not limited to the listed values, and other unlisted values ​​within the numerical range are also applicable.

[0052] In some optional examples, the mass ratio of the aluminum nitrate to deionized water is 1:10.

[0053] In some optional examples, the mass fraction of the ammonia solution is 10-12 wt.%, for example, it can be 10.0 wt.%, 10.2 wt.%, 10.4 wt.%, 10.6 wt.%, 10.8 wt.%, 11.0 wt.%, 11.2 wt.%, 11.4 wt.%, 11.6 wt.%, 11.8 wt.% or 12.0 wt.%, but is not limited to the listed values, and other unlisted values ​​within this numerical range are also applicable.

[0054] In some optional examples, the holding time of immersing in the Al(OH)3 suspension is 30-40 min, for example, it can be 30.0 min, 31.0 min, 32.0 min, 33.0 min, 34.0 min, 35.0 min, 36.0 min, 37.0 min, 38.0 min, 39.0 min or 40.0 min, but is not limited to the listed values, and other unlisted values ​​within the numerical range are also applicable.

[0055] In some optional examples, the calcination time is 2-3h, for example, it can be 2.0h, 2.1h, 2.2h, 2.3h, 2.4h, 2.5h, 2.6h, 2.7h, 2.8h, 2.9h or 3.0h, but is not limited to the listed values, and other unlisted values ​​within the numerical range are also applicable.

[0056] In a second aspect, the present invention provides high-strength and high-modulus inorganic mineral fibers prepared using water-quenched slag and obtained by the preparation method described in the first aspect.

[0057] Compared with the prior art, the present invention has the following beneficial effects:

[0058] (1) During the high-temperature melting process, the BO3 unit in B2O3 reacts chemically with the silicon-oxygen bond in the SiO4 unit to form a new BO-Si bond. The formation of the BO-Si bond significantly increases the cross-linking degree of the glass network. This cross-linking not only enhances the structural stability of the material, but also improves the chemical stability and chemical corrosion resistance of the melt. At the same time, the BOB bond further enhances the cross-linking degree of the glass network, making the fiber denser and more uniform.

[0059] (2) Y in Y2O3 3+ By combining with oxygen bridge bonds, the local atomic arrangement order required for crystal growth is destroyed, and the high electric field strength of the ions can significantly inhibit the precipitation of crystal phases in the melt and prevent the formation and growth of crystal nuclei. 3+ Ions in the melt can interfere with the aggregation tendency of the crystal phase, ensuring that the glass maintains its amorphous structural characteristics during the cooling process. 3＋ The high electric field strength of the ions can form stable BO-Si and BOB bonds with B2O3, enhancing the degree of cross-linking while reducing the tendency of crystal precipitation;

[0060] (3) During the high-temperature melting process, V2O5, as a transition metal oxide, vanadium ions can 5+ and V 4+The dynamic transformation between the two oxidation states and this variable valence state enable V2O5 to play the role of a redox buffer in the molten glass system, regulating the redox balance in the melt by capturing or releasing electrons. The redox buffering effect reduces the phase separation phenomenon caused by excessive oxidation or excessive reduction of components in the melt, thereby ensuring the chemical uniformity of the glass system. BRIEF DESCRIPTION OF THE DRAWINGS

[0061] Figure 1 This is a SEM image of the inorganic mineral fiber prepared using water-quenched slag in Example 1 of the present invention (scale: 20 μm);

[0062] Figure 2 This is a SEM image of the inorganic mineral fiber prepared using water-quenched slag in Example 1 of the present invention (scale: 5 μm);

[0063] Figure 3 This is a TEM image of the inorganic mineral fiber prepared using water-quenched slag in Example 1 of the present invention;

[0064] Figure 4 This is the SEM image of the composite oxide modifier in Example 1 of the present invention. DETAILED DESCRIPTION

[0065] The technical solutions of the present invention are described in detail below in conjunction with specific embodiments and their accompanying drawings. The embodiments described herein are specific embodiments of the present invention and are used to illustrate the concept of the present invention; these descriptions are explanatory and exemplary and should not be understood as limiting the embodiments of the present invention and the scope of protection of the present invention. In addition to the embodiments described herein, those skilled in the art can also adopt other obvious technical solutions based on the contents disclosed in the claims of this application and its specification, including technical solutions that adopt any obvious replacements and modifications to the embodiments described herein.

[0066] The chemical reagents used in the examples and comparative examples of the present invention are all commercially available products and have not been subjected to any further purification treatment.

[0067] Example 1

[0068] This embodiment provides a method for preparing high-strength and high-modulus inorganic mineral fibers using water-quenched slag, the method specifically comprising the following steps:

[0069] Step S1: placing the water-quenched slag raw material into a vibrating screen for particle classification, retaining the medium-sized particle portion of 100-1000 μm, pouring 100 g of the water-quenched slag of the medium-sized particle portion into 500 g of lithium chloride solution, collecting the floated portion, filtering and washing it, and then fully drying it at 123° C. for 12.6 hours, placing 50 g of the dried floated water-quenched slag into 500 mL of 3.3 wt.% hydrochloric acid solution, fully stirring it at room temperature for 2.2 hours, filtering and washing it, and then fully drying it at 123° C. for 13.0 hours to obtain acid-washed water-quenched slag particles, crushing 50 g of the acid-washed water-quenched slag particles to less than 50 μm, and then mixing it with 3.5 g of Na2CO3 and 1.5 g of Fe2O3, heating it to 880° C. and continuously calcining it for 2.2 hours. After the calcination, cooling it to room temperature to obtain high-temperature sintered water-quenched slag;

[0070] Step S2, 55g, 9wt.% boric acid solution and 58g, 13wt.% yttrium nitrate solution were mixed to obtain a mixed solution, and then 2g of vanadium pentoxide was dissolved in 30g, 20wt.% ammonia water, and added to the mixed solution. After stirring evenly, the pH was adjusted to 8.0 with ammonia water, and stirring was continued for 35min to complete the precipitation reaction. After filtering and washing, the mixture was dried at 85°C for 10.5h to obtain a wet powder precursor, and then 8g of H3BO3, 6g of Y2O3 and 4g of V2O5 were mixed to obtain a mixture. The mixture and 27g of the wet powder precursor were put into a ball mill and ethanol was added. After ball milling for 2.3h, the mixture was calcined at 850°C for 4.2h to obtain a composite oxide modifier;

[0071] Step S3: 62 g of high-temperature sintered water-quenched slag, 28 g of a composite oxide modifier, and 13 g of borax were mixed and ball-milled for 45 minutes to obtain a mixture. The mixture was heated to 1500° C., and the molten material was drawn into fibers using a fiber blowing device. The fibers were then annealed in an argon atmosphere at 450° C. for 65 minutes at a cooling rate of 3° C. / min to obtain annealed fibers.

[0072] Step S4, soaking the annealed fiber in anhydrous ethanol, ultrasonically cleaning to remove surface contaminants, and then drying it at 122°C for 2.4 hours, dissolving 10g of aluminum nitrate in 100g of deionized water, stirring until dissolved, and then adding 10.5wt.% ammonia solution to adjust the pH to 7.5 to obtain an Al(OH)3 suspension, immersing the dried annealed fiber in the Al(OH)3 suspension, keeping it for 33 minutes, then taking out the annealed fiber, and calcining it at 880°C for 2.4 hours to obtain a high-strength and high-modulus inorganic mineral fiber prepared using water-quenched slag.

[0073] Figure 1 This is the SEM image of the inorganic mineral fiber prepared in this example. It can be seen that the fiber surface is smooth, the diameter is uniform, and there are no obvious cracks or particles attached; Figure 2This is a SEM image of the inorganic mineral fiber prepared using water-quenched slag in Example 1 of the present invention (scale: 5 μm); Figure 3 This is a TEM image of the inorganic mineral fiber prepared using water-quenched slag in Example 1 of the present invention; Figure 4 This is the SEM image of the composite oxide modifier in Example 1 of the present invention.

[0074] Example 2

[0075] This embodiment provides a method for preparing high-strength and high-modulus inorganic mineral fibers using water-quenched slag, the method specifically comprising the following steps:

[0076] Step S1: placing the water-quenched slag raw material into a vibrating screen for particle classification, retaining the medium-sized particle portion of 100-1000 μm, pouring 100 g of the water-quenched slag of the medium-sized particle portion into 550 g of lithium chloride solution, collecting the floated portion, filtering and washing, and then fully drying it at 120° C. for 12.0 hours, placing 60 g of the dried floated water-quenched slag into 600 mL of 3.7 wt.% hydrochloric acid solution, fully stirring it at room temperature for 2.0 hours, filtering and washing, and then fully drying it at 120° C. for 12.5 hours to obtain acid-washed water-quenched slag particles, crushing 70 g of the acid-washed water-quenched slag particles to less than 50 μm, and then mixing them with 5.6 g of Na2CO3 and 2.1 g of Fe2O3, heating them to 850° C. and continuously calcining them for 2.6 hours. After the calcination, cooling them to room temperature to obtain high-temperature sintered water-quenched slag;

[0077] Step S2, 55g, 9wt.% boric acid solution and 58g, 13wt.% yttrium nitrate solution were mixed to obtain a mixed solution, and then 2g of vanadium pentoxide was dissolved in 30g, 20wt.% ammonia water, and added to the mixed solution. After stirring evenly, the pH was adjusted to 8.5 with ammonia water, and stirring was continued for 30min to complete the precipitation reaction. After filtering and washing, the mixture was dried at 80°C for 11.1h to obtain a wet powder precursor, and then 8g of H3BO3, 6g of Y2O3 and 4g of V2O5 were mixed to obtain a mixture. The mixture and 27g of the wet powder precursor were put into a ball mill and ethanol was added. After ball milling for 2.6h, the mixture was calcined at 890°C for 4.8h to obtain a composite oxide modifier;

[0078] Step S3: 67 g of high-temperature sintered water-quenched slag, 30 g of a composite oxide modifier, and 10 g of borax were mixed and ball-milled for 50 minutes to obtain a mixture. The mixture was heated to 1450° C., and the molten material was drawn into fibers using a fiber blowing device. The fibers were then annealed in an argon atmosphere at 400° C. for 70 minutes at a cooling rate of 3° C. / min to obtain annealed fibers.

[0079] Step S4, soaking the annealed fiber in anhydrous ethanol, ultrasonically cleaning to remove surface contaminants, and then drying it at 127°C for 2.0 hours, dissolving 10g of aluminum nitrate in 100g of deionized water, stirring until dissolved, and then adding 11.0wt.% ammonia solution to adjust the pH to 7.5 to obtain an Al(OH)3 suspension, immersing the dried annealed fiber in the Al(OH)3 suspension, keeping it for 30 minutes, then taking out the annealed fiber, and calcining it at 850°C for 2.1 hours to obtain a high-strength and high-modulus inorganic mineral fiber prepared using water-quenched slag.

[0080] Example 3

[0081] This embodiment provides a method for preparing high-strength and high-modulus inorganic mineral fibers using water-quenched slag, the method specifically comprising the following steps:

[0082] Step S1: placing the water-quenched slag raw material into a vibrating screen for particle classification, retaining the medium-sized particle portion of 100-1000 μm, pouring 100 g of the water-quenched slag of the medium-sized particle portion into 600 g of lithium chloride solution, collecting the floated portion, filtering and washing, and then fully drying it at 126° C. for 13.4 hours, placing 70 g of the dried floated water-quenched slag into 700 mL of 4.0 wt.% hydrochloric acid solution, fully stirring it at room temperature for 2.6 hours, filtering and washing, and then fully drying it at 126° C. for 14.0 hours to obtain acid-washed water-quenched slag particles, crushing 60 g of the acid-washed water-quenched slag particles to less than 50 μm, and then mixing them with 4.2 g of Na2CO3 and 2.4 g of Fe2O3, heating them to 910° C. and continuously calcining them for 2.0 hours, and cooling them to room temperature after the calcination to obtain high-temperature sintered water-quenched slag;

[0083] Step S2, 55g, 9wt.% boric acid solution and 58g, 13wt.% yttrium nitrate solution were mixed to obtain a mixed solution, and then 2g of vanadium pentoxide was dissolved in 30g, 20wt.% ammonia water, and added to the mixed solution. After stirring evenly, the pH was adjusted to 8.4 with ammonia water, and stirring was continued for 50min to complete the precipitation reaction. After filtering and washing, the mixture was dried at 94°C for 12.0h to obtain a wet powder precursor, and then 8g of H3BO3, 6g of Y2O3 and 4g of V2O5 were mixed to obtain a mixture. The mixture and 27g of the wet powder precursor were put into a ball mill and ethanol was added. After ball milling for 2.0h, the mixture was calcined at 950°C for 5.4h to obtain a composite oxide modifier;

[0084] Step S3: 60 g of high-temperature sintered water-quenched slag, 24 g of a composite oxide modifier, and 16 g of borax were mixed and ball-milled for 51 minutes to obtain a mixture. The mixture was heated to 1550° C., and the molten material was drawn into fibers using a fiber blowing device. The fibers were then annealed in an argon atmosphere at 410° C. for 71 minutes at a cooling rate of 3° C. / min to obtain annealed fibers.

[0085] Step S4, soaking the annealed fiber in anhydrous ethanol, ultrasonically cleaning to remove surface contaminants, and then drying it at 120°C for 2.8 hours, dissolving 10g of aluminum nitrate in 100g of deionized water, stirring until dissolved, and then adding 11.3wt.% ammonia solution to adjust the pH to 7.5 to obtain an Al(OH)3 suspension, immersing the dried annealed fiber in the Al(OH)3 suspension, keeping it for 36 minutes, then taking out the annealed fiber, and calcining it at 950°C for 2.7 hours to obtain a high-strength and high-modulus inorganic mineral fiber prepared using water-quenched slag.

[0086] Example 4

[0087] This embodiment provides a method for preparing high-strength and high-modulus inorganic mineral fibers using water-quenched slag, the method specifically comprising the following steps:

[0088] Step S1: placing the water-quenched slag raw material into a vibrating screen for particle classification, retaining the medium-sized particle portion of 100-1000 μm, pouring 100 g of the water-quenched slag of the medium-sized particle portion into 580 g of lithium chloride solution, collecting the floated portion, filtering and washing, and then fully drying it at 130° C. for 14.0 hours, placing 60 g of the dried floated water-quenched slag into 600 mL of 3.0 wt.% hydrochloric acid solution, fully stirring it at room temperature for 3.0 hours, filtering and washing, and then fully drying it at 130° C. for 12.7 hours to obtain acid-washed water-quenched slag particles, crushing 50 g of the acid-washed water-quenched slag particles to less than 50 μm, and then mixing them with 5 g of Na2CO3 and 2.0 g of Fe2O3, heating them to 950° C. and continuously calcining them for 3.0 hours, and cooling them to room temperature after the calcination to obtain high-temperature sintered water-quenched slag;

[0089] Step S2, 55g, 9wt.% boric acid solution and 58g, 13wt.% yttrium nitrate solution were mixed to obtain a mixed solution, and then 2g of vanadium pentoxide was dissolved in 30g, 20wt.% ammonia water, and added to the mixed solution. After stirring evenly, the pH was adjusted to 8.3 with ammonia water, and stirring was continued for 40min to complete the precipitation reaction. After filtering and washing, it was placed at 100°C for 10.9h to obtain a wet powder precursor, and then 8g of H3BO3, 6g of Y2O3 and 4g of V2O5 were mixed to obtain a mixture. The mixture and 27g of the wet powder precursor were put into a ball mill and ethanol was added. After ball milling for 3.0h, it was placed at 910°C for calcination for 6.0h to obtain a composite oxide modifier;

[0090] Step S3: 70 g of high-temperature sintered water-quenched slag, 20 g of a composite oxide modifier, and 20 g of borax are mixed and ball-milled for 60 minutes to obtain a mixture. The mixture is heated to 1490° C., and the molten material is drawn into fibers using a fiber blowing device. The fibers are then annealed in an argon atmosphere at 500° C. for 80 minutes at a cooling rate of 3° C. / min to obtain annealed fibers.

[0091] Step S4, soaking the annealed fiber in anhydrous ethanol, ultrasonically cleaning to remove surface contaminants, and then drying it at 130°C for 3.0 hours, dissolving 10g of aluminum nitrate in 100g of deionized water, stirring until dissolved, and then adding 12.0wt.% ammonia solution to adjust the pH to 7.5 to obtain an Al(OH)3 suspension, immersing the dried annealed fiber in the Al(OH)3 suspension, keeping it for 40 minutes, then taking out the annealed fiber, and calcining it at 910°C for 3.0 hours to obtain a high-strength and high-modulus inorganic mineral fiber prepared using water-quenched slag.

[0092] Comparative Example 1

[0093] This comparative example provides a method for preparing high-strength and high-modulus inorganic mineral fibers using water-quenched slag. The difference from Example 1 is that the mass of H3BO3 in step S2 is adjusted to 15g, which is 7g more than that in Example 1. The other process parameters and operating conditions are exactly the same as those in Example 1.

[0094] Comparative Example 2

[0095] This comparative example provides a method for preparing high-strength and high-modulus inorganic mineral fibers using water-quenched slag. The difference from Example 1 is that the mass of H3BO3 in step S2 is adjusted to 1g, which is 7g less than that in Example 1. The other process parameters and operating conditions are exactly the same as those in Example 1.

[0096] Comparative Example 3

[0097] This comparative example provides a method for preparing high-strength and high-modulus inorganic mineral fibers using water-quenched slag. The difference from Example 1 is that the mass of V2O5 in step S2 is adjusted to 7g, which is 3g more than that in Example 1. The other process parameters and operating conditions are exactly the same as those in Example 1.

[0098] Comparative Example 4

[0099] This comparative example provides a preparation method for high-strength and high-modulus inorganic mineral fibers using water-quenched slag. The difference from Example 1 is that the mass of V2O5 in step S2 is adjusted to 1g, which is 3g less than that in Example 1. The other process parameters and operating conditions are exactly the same as those in Example 1.

[0100] The test standard for the tensile strength and elastic modulus of the inorganic mineral fiber prepared in the present invention is GB / T1447-2005. The test results are shown in Table 1.

[0101] Table 1 Test results of high-strength and high-modulus inorganic mineral fibers prepared in Examples 1-4 and Comparative Examples 1-4

[0102]

[0103] It can be seen from the data in the table that compared with Example 1, the tensile strength and elastic modulus of Comparative Example 1 are both reduced; the tensile strength and elastic modulus of Comparative Example 2 are both reduced. An appropriate amount of B2O3 can enhance the cross-linking of the network through BO3 and BO4 units. In Comparative Example 1, excessive B2O3 will cause the proportion of BO3 units in the glass network to increase significantly, and the proportion of BOB bonds will also increase, but the mechanical strength of BOB bonds is low. At the same time, excessive B2O3 will reduce the viscosity of the melt. Although it helps fiber drawing, the excessive fluidity of the melt may cause component separation or localized crystal precipitation. The presence of crystal precipitation will become a stress concentration point inside the fiber, reducing the tensile strength and elastic modulus. When borates coexist with other oxides, the O in the oxides 2- Ions can react with BO3 units to convert part of BO3 into BO4 tetrahedral units. BO4 units have strong network bonding ability. During the melting process, the oxygen atoms of the BO4 units are shared with the oxygen atoms of the SiO4 units to generate Si-OB bonds. This bridge bond structure enhances the cross-linking degree of the network, improves the mechanical strength and chemical stability. In Comparative Example 2, H3BO3 is insufficient, so the tensile strength and elastic modulus of the inorganic mineral fiber decrease.

[0104] Compared to Example 1, the tensile strength and elastic modulus of Comparative Example 3 decreased; the tensile strength and elastic modulus of Comparative Example 4 also decreased. Excessive V2O5 can cause its solubility in the melt to exceed its saturation limit, potentially leading to localized V2O5 enrichment and even the precipitation of vanadium oxide crystals (such as V2O4 or V2O5 crystals). The presence of these crystals introduces defects into the fiber, creating stress concentration points and reducing the tensile strength. Consequently, the tensile strength and elastic modulus decreased in Comparative Example 3. V2O5, through its variable valence state, provides a redox buffer, maintaining redox equilibrium in the melt. Insufficient V2O5 can increase the proportion of peroxides or suboxides in the melt, increasing the risk of crystal precipitation and reducing the proportions of VO-Si and VOB. Consequently, the tensile strength and elastic modulus decreased in Comparative Example 4.

[0105] The above description is only a specific embodiment of the present invention, but the protection scope of the present invention is not limited thereto. Those skilled in the art should understand that any changes or substitutions that can be easily thought of by those skilled in the art within the technical scope disclosed by the present invention fall within the protection scope and disclosure scope of the present invention.

Claims

1. A method for preparing high-strength and high-modulus inorganic mineral fibers using water-quenched slag, characterized in that: The preparation method is: Step S1: Classifying the water-quenched slag raw material into particles, retaining the medium-sized particles and pouring them into a lithium chloride solution, collecting the floating particles, and placing the dried floating water-quenched slag into a hydrochloric acid solution to obtain acid-washed water-quenched slag particles. The acid-washed water-quenched slag particles are crushed to a particle size below a target size, and then mixed with Na2CO3 and Fe2O3 and calcined to obtain high-temperature sintered water-quenched slag; Step S2, mixing a boric acid solution with an yttrium nitrate solution to obtain a mixed solution, dissolving vanadium pentoxide in aqueous ammonia and adding the solution to the mixed solution, adjusting the pH to 8-8.5 to obtain a wet powder precursor, mixing H3BO3, Y2O3 and V2O5 to obtain a mixture, ball-milling the mixture with the wet powder precursor and calcining the mixture to obtain a composite oxide modifier; Step S3, mixing the high-temperature sintered water-quenched slag, the composite oxide modifier, and borax, ball-milling the mixture, and then melt-drawing the mixture into fibers, which are then annealed in an argon atmosphere to obtain annealed fibers; Step S4, immersing the annealed fiber in anhydrous ethanol, ultrasonically cleaning and drying, dissolving aluminum nitrate in deionized water, adjusting the pH to 7.5 to obtain an Al(OH)3 suspension, immersing the dried annealed fiber in the Al(OH)3 suspension, keeping it for a certain period of time, then taking out the annealed fiber and calcining it to obtain a high-strength and high-modulus inorganic mineral fiber prepared using water-quenched slag.

2. The method for preparing high-strength and high-modulus inorganic mineral fibers using water-quenched slag according to claim 1, characterized in that: In step S1, The particle size of the medium particle part is 100-1000 μm; The density of the lithium chloride solution is 1.3 g / cm 3 .

3. The method for preparing high-strength and high-modulus inorganic mineral fibers using water-quenched slag according to claim 1, characterized in that: In step S1, The solid-liquid ratio of the floated portion to the hydrochloric acid solution is 1 g:10 mL.

4. The method for preparing high-strength and high-modulus inorganic mineral fibers using water-quenched slag according to claim 1, characterized in that: In step S1, The target particle size is 50 μm; The mass of the Na2CO3 is 5-10% of the mass of the pickling water quenching slag particles; The mass of the Fe2O3 is 2-4% of the mass of the pickling water-quenched slag particles.

5. The method for preparing high-strength and high-modulus inorganic mineral fibers using water-quenched slag according to claim 1, characterized in that: In step S2, In the yttrium nitrate solution, the mass ratio of yttrium nitrate hexahydrate to deionized water is 4:25; The mass ratio of the boric acid, yttrium nitrate hexahydrate and vanadium pentoxide is 5:8:

2.

6. The method for preparing high-strength and high-modulus inorganic mineral fibers using water-quenched slag according to claim 1, characterized in that: In step S2, The mass ratio of H3BO3, Y2O3, and V2O5 is 4:3:2; The mass ratio of the mixture to the wet powder precursor is 2:

3.

7. The method for preparing high-strength and high-modulus inorganic mineral fibers using water-quenched slag according to claim 1, characterized in that: In step S3, The mass ratio of the high-temperature sintered water-quenched slag, the composite oxide modifier and borax is (60-70): (20-30): (10-20); The holding time of the annealing treatment is 60-80 minutes, and the cooling rate is 3°C / min.

8. The method for preparing high-strength and high-modulus inorganic mineral fibers using water-quenched slag according to claim 1, characterized in that: In step S4, The mass ratio of the aluminum nitrate to deionized water is 1:

10.

9. The method for preparing high-strength and high-modulus inorganic mineral fibers using water-quenched slag according to claim 1, characterized in that: In step S4, The immersion in the Al(OH)3 suspension is maintained for 30-40 minutes; The calcination time is 2-3 hours.

10. The high-strength and high-modulus inorganic mineral fiber prepared by using water-quenched slag and obtained by the preparation method according to any one of claims 1 to 9.

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