A synergistic rare earth composite energy health care product and a preparation method thereof

Abstract

The present application relates to the technical field of health-care materials, and discloses a rare earth composite energy health-care product based on synergy and a preparation method thereof, which comprises monazite fine powder 10 parts by weight, silico-aluminate composite network forming agent 75-80 parts by weight, in-situ reduction and network modifier 5-10 parts by weight, and pore forming agent 3-5 parts by weight; the preparation method comprises the following steps: crushing and grading the raw ore to obtain fine powder by intercepting high-density radioactive associated ore; mixing and kneading the fine powder and the remaining components to form a green body; performing three-stage step calcination to sequentially complete low-temperature pore forming, high-temperature magnesium hot reduction to generate lattice oxygen vacancies, and introduction of high-temperature water vapor to promote the generation of amorphous liquid phase to solid-solution-embed radioactive nuclides; and finally, forced air cooling and depolymerization and crushing are performed to obtain the finished product. The present application effectively reduces the radioactivity background of the material, blocks the physical channel for the escape of decay gas, and enables the product to have the functions of safe and stable far-infrared radiation and release of negative oxygen ions.

Description

Technical Field

[0001] This invention relates to the field of health care materials technology, specifically to a rare earth composite energy health care product based on synergy and its preparation method. Background Technology

[0002] Natural rare earth minerals, due to their weak radioactivity and pyroelectric properties, can release negative oxygen ions and radiate far-infrared rays into the surrounding environment, and are currently used in the preparation of health care materials. However, natural rare earth ores often contain radioactive minerals containing thorium and uranium. Existing processes mostly employ conventional physical crushing and mixing, which makes it difficult to effectively separate the high-density radioactive associated phases in the raw ore. This results in finished products with a high background of radioactivity, making it difficult to meet relevant safety standards.

[0003] Meanwhile, radioactive nuclides within the material will produce radioactive gases such as radon during natural decay. Conventional rare-earth composite materials typically have porous internal structures, lacking a dense physical encapsulation between components. This structural feature provides a physical channel for the outward diffusion of decay gases, making radon easily released into the external environment, posing a potential safety hazard. Furthermore, most existing rare-earth health products directly utilize the initial physical properties of raw mineral powders without specifically modifying or reconstructing the internal crystal structure. Due to the lack of lattice defects within the material, effective spontaneous polarization micro-regions cannot be formed, resulting in low efficiency in converting environmental heat energy into far-infrared radiation. Insufficient surface electric field strength also limits its ionization ability of water molecules in the air, leading to a low concentration of negative oxygen ions released from the finished product and poor performance stability during long-term use. Summary of the Invention

[0004] The technical problem solved by this invention is to provide a rare earth composite health care material with far-infrared radiation energy and negative oxygen ion release function, and to solve the technical problems of excessive background radioactivity and radioactive decay gas release in existing related materials.

[0005] To address the above problems, the present invention provides the following technical solution:

[0006] The first aspect of this invention provides a rare earth composite energy health care product based on synergy, wherein the rare earth composite energy health care product based on synergy is formed by mixing, calcining and polymerizing the following raw materials in parts by weight: monazite fine powder: 10 parts; aluminosilicate composite network forming agent: 75-80 parts; in-situ reduction and network modification agent: 5-10 parts; pore-forming agent: 3-5 parts.

[0007] Preferably, the raw material is composed of the following components in parts by weight: 10 parts monazite fine powder; 78 parts aluminosilicate composite network forming agent; 8 parts in-situ reduction and network modification agent; and 4 parts pore-forming agent.

[0008] Preferably, the aluminosilicate composite network forming agent is an inorganic mineral powder mixture, which is composed of microporous basalt-type volcanic rock or andesite-type volcanic rock, hematite-type ochre, porphyritic andesite-type maifanite, and alum-type alum, and the mass ratio of the microporous basalt-type volcanic rock or andesite-type volcanic rock, the hematite-type ochre, the porphyritic andesite-type maifanite, and the alum-type alum is (35-40):(10-15):(15-16):(10-15).

[0009] Preferably, the in-situ reduction and network modifier is composed of metallic magnesium powder and light magnesium oxide, and the mass ratio of the metallic magnesium powder to light magnesium oxide is 1:1 to 1:2; the purity of the metallic magnesium powder is greater than 99.0% and the particle size is 200-300 mesh.

[0010] Preferably, the pore-forming agent is industrial-grade urea powder or ammonium carbonate powder; the monazite fine powder is natural monazite light phase fine powder with an aerodynamic equivalent diameter D90 ≤ 10 μm.

[0011] A second aspect of this invention provides a method for preparing the above-mentioned rare earth composite energy health product based on synergy, comprising the following steps:

[0012] Natural monazite ore is coarsely crushed and then subjected to airflow ultrafine grinding and dynamic classification to collect light phase fine powder as the monazite fine powder raw material.

[0013] The monazite fine powder, aluminosilicate composite network forming agent, in-situ reducing and network modifying agent and pore-forming agent are dry-mixed evenly to obtain dry powder material, which is then sprayed with deionized water and kneaded to form mud. After vacuum extrusion molding, cutting and natural air drying, block blanks are obtained.

[0014] The block-shaped billet is loaded into a kiln and subjected to three-stage stepped firing, which proceeds in sequence as follows: low-temperature exhaust to decompose the pore-forming agent, firing under a high-temperature inert protective atmosphere, and firing under a high-temperature steam atmosphere to obtain high-temperature clinker blocks.

[0015] The high-temperature clinker blocks are removed from the kiln and subjected to forced air cooling to room temperature. Finally, they are crushed, deagglomerated and pulverized by air jet milling, and the powder is collected to obtain the rare earth composite energy health care product based on synergy.

[0016] Preferably, the process parameters for the airflow ultrafine pulverization and dynamic classification are as follows: the process is carried out in a fluidized bed jet mill, the pulverizing air source pressure is controlled at 0.6-0.8 MPa, the speed of the dynamic airflow classifier wheel is set at 3000-4500 r / min, and the system induced draft volume is controlled at 15-25 m3 / min.

[0017] Preferably, the amount of deionized water injected accounts for 10%-15% of the total mass of the dry powder material; the vacuum degree of the vacuum extrusion molding is -0.06MPa to -0.09MPa; the environmental conditions for natural air drying are: temperature 20-30℃, relative humidity 40%-60%, and air drying time 24-48h.

[0018] Preferably, the specific process conditions for the three-stage stepped roasting are as follows:

[0019] First stage: Maintain a constant temperature of 300-500℃ for 1.0-2.5 hours;

[0020] Second stage: Proceed to the high-temperature roasting zone preheated to 1450-1550℃, and introduce nitrogen or argon gas with a purity ≥99.9% as a protective atmosphere, and maintain the temperature for 0.5-1.5 hours;

[0021] Third stage: Stop the protective atmosphere at 1450-1550℃, switch to high-temperature steam at a pressure of 0.2-0.5MPa, and continue constant temperature roasting for 1.5-3.0h.

[0022] Preferably, the cooling rate of the forced air cooling treatment is controlled at 50-100℃ / min; and the particle size D90 of the collected powder is controlled at 18-48μm.

[0023] This invention provides a rare earth composite energy health product based on synergy and its preparation method. It has the following beneficial effects:

[0024] 1. This invention utilizes airflow ultrafine grinding and dynamic classification processes to physically trap high-density radioactive associated minerals in the raw ore by taking advantage of the difference between centrifugal force and airflow drag force, thereby reducing the background radioactivity level of the material. At the same time, high-temperature water vapor is introduced during the roasting stage to promote the formation of amorphous liquid phase of aluminosilicates, which solidifies and embeds radioactive nuclides in a dense three-dimensional network structure, blocking the physical channels for the outward diffusion of radioactive decay gases and improving the safety of the product.

[0025] 2. This invention utilizes the thermal reduction of magnesium powder by vaporizing it in a high-temperature inert atmosphere to generate high-pressure magnesium vapor, causing the transition metal elements within the matrix to undergo heterovalent substitution and release oxygen atoms to generate oxygen vacancies. Combined with forced air cooling to prevent thermodynamic relaxation of lattice defects, the long-range ordered structure of the crystal is destroyed in situ, establishing non-centrosymmetric spontaneously polarized microregions within the material. This gives the product the physical characteristic of converting thermal energy into far-infrared radiation energy in the 8 to 10 micrometer wavelength range.

[0026] 3. This invention utilizes polarized micro-regions established within the material to create a polarized micro-electric field on the powder surface. Under the dual excitation of fundamental decay radiation and far-infrared resonant emission, the ionization potential of water molecules adsorbed on the powder surface is reduced. Water molecules undergo electrolysis under the micro-electric field, and the free electrons generated by electrolysis are repelled by the electric field and captured by oxygen molecules in the air to generate negative oxygen ions, thereby achieving continuous and stable ionization and release of negative oxygen ions from the surrounding air by the material. Attached Figure Description

[0027] Figure 1 This is a distribution diagram of the specific activity of each phase material before and after the classification of the present invention;

[0028] Figure 2 This is a comparison chart of the specific surface area and radon exudation rate of the intermediate state billet and the final clinker of the present invention;

[0029] Figure 3 This is a comparison chart of the total α and total β radioactivity specific activities of the various powder products of this invention;

[0030] Figure 4 This is a comparison chart of the normal total emissivity of the various powder products of this invention in the 8 to 10 μm band;

[0031] Figure 5 This is a comparison diagram of the peak polarization microcurrent of each powder product of the present invention; Figure 6 This is a comparison chart of the negative oxygen ion release concentrations of the various powder products of this invention. Detailed Implementation

[0032] The technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the accompanying drawings. Obviously, the described embodiments are only some embodiments of the present invention, and not all embodiments. Based on the embodiments of the present invention, all other embodiments obtained by those skilled in the art without creative effort are within the scope of protection of the present invention.

[0033] Preparation Examples 1-3:

[0034] Preparation Example 1:

[0035] This preparation example provides a method for preparing an aluminosilicate composite network forming agent and an in-situ reduction and network modifying agent, including the following steps:

[0036] (1) Preparation of aluminosilicate composite network forming agent: According to the mass fraction, weigh 40 parts of microporous basalt type volcanic rock, 15 parts of hematite type ochre, 15 parts of porphyritic andesite type maifanite, and 10 parts of alum mineral type alum; put the above four inorganic mineral powders into a V-type mixer and mix evenly to obtain a total mass of 80 parts of aluminosilicate composite network forming agent.

[0037] (2) Preparation of in-situ reduction and network modifier: According to the mass fraction, weigh 2.5 parts of metallic magnesium powder with a purity greater than 99.0% and a particle size of 200-300 mesh, and weigh 2.5 parts of light magnesium oxide (the mass ratio of metallic magnesium powder to light magnesium oxide is controlled at 1:1); place the two in a closed mixer under inert atmosphere protection and mix evenly to obtain an in-situ reduction and network modifier with a total mass of 5 parts.

[0038] Preparation Example 2:

[0039] This preparation example provides a method for preparing an aluminosilicate composite network forming agent and an in-situ reduction and network modifying agent, including the following steps:

[0040] (1) Preparation of aluminosilicate composite network forming agent: According to the mass fraction, weigh 38 parts of microporous basalt type volcanic rock, 12 parts of hematite type ochre, 16 parts of porphyritic andesite type maifanite, and 12 parts of alum mineral type alum; put the above four inorganic mineral powders into a V-type mixer and mix evenly to obtain a total mass of 78 parts of aluminosilicate composite network forming agent.

[0041] (2) Preparation of in-situ reduction and network modifier: According to the mass fraction, weigh 3.2 parts of metallic magnesium powder with a purity greater than 99.0% and a particle size of 200-300 mesh, and weigh 4.8 parts of light magnesium oxide (the mass ratio of metallic magnesium powder to light magnesium oxide is controlled at 1:1.5); place the two in a closed mixer under inert atmosphere protection and mix evenly to obtain an in-situ reduction and network modifier with a total mass of 8 parts.

[0042] Preparation Example 3:

[0043] This preparation example provides a method for preparing an aluminosilicate composite network forming agent and an in-situ reduction and network modifying agent, including the following steps:

[0044] (1) Preparation of aluminosilicate composite network forming agent: According to the mass fraction, weigh 40 parts of andesite-type volcanic rock, 15 parts of hematite-type ochre, 15 parts of porphyritic andesite-type maifanite, and 10 parts of alum-type alum. Put the above four inorganic mineral powders into a V-type mixer and mix them evenly to obtain a total mass of 80 parts of aluminosilicate composite network forming agent.

[0045] (2) Preparation of in-situ reduction and network modifier: According to the mass fraction, weigh 3.3 parts of metallic magnesium powder with a purity greater than 99.0% and a particle size of 200-300 mesh, and weigh 6.7 parts of light magnesium oxide (the mass ratio of metallic magnesium powder to light magnesium oxide is about 1:2); place the two in a closed mixer under inert atmosphere protection and mix evenly to obtain an in-situ reduction and network modifier with a total mass of 10 parts. Examples 1-3: Example 1:

[0046] This embodiment provides a method for preparing a rare earth composite energy health product based on synergy, including the following steps:

[0047] (1) Physical cost reduction and classification: After coarse crushing of natural monazite ore, it is continuously fed into a fluidized bed jet mill for ultrafine crushing. The pressure of the crushing air source is controlled at 0.6MPa; the dynamic air classifier at the top is turned on, the speed is set to 3000r / min, and the system induced draft is controlled at 15m³. 3 / min; collect light phase fine powder with an aerodynamic equivalent diameter D90≤10μm as raw material.

[0048] (2) Homogeneous mixing and porous molding: According to the mass fraction, weigh 10 parts of the above-mentioned monazite fine powder, 75 parts of the aluminosilicate composite network forming agent obtained in Preparation Example 1, 5 parts of the in-situ reduction and network modifier obtained in Preparation Example 1, and 3 parts of industrial-grade urea powder as a pore-forming agent; put the above dry powder materials into a V-type mixer, set the speed to 15 r / min, and dry mix for 20 min; then transfer to a biaxial kneader, uniformly spray in 10% of the total mass of dry powder materials with deionized water, knead for 15 min to form mud; use a vacuum extruder to extrude and form under a vacuum of -0.06 MPa, cut into block blanks with a thickness of 50 mm, and air dry naturally in an environment with a temperature of 20℃ and a relative humidity of 40% for 24 h.

[0049] (3) Atmosphere decoupling dynamic calcination: The dried billet is loaded into a refractory sagger and sent into a tunnel kiln for three-stage stepped calcination: First, it is kept at a constant temperature of 300℃ for 1.0h, and the kiln exhaust air makes the pore-forming agent completely decompose and form pores; then the billet is directly pushed into the high-temperature calcination zone that has been preheated to 1450℃, and high-purity nitrogen with a purity of ≥99.9% is introduced as a protective atmosphere and kept at a constant temperature for 0.5h, so that the magnesium powder is vaporized and thermal shock reduction occurs in the pores; then the nitrogen is stopped at 1450℃, and high-temperature steam with a pressure of 0.2MPa is introduced, and the constant temperature calcination continues for 1.5h, so that the aluminosilicate forms a liquid phase and the pores collapse and solid solution occur.

[0050] (4) Quenching and deagglomeration restoration: The high-temperature clinker blocks that have been roasted are removed from the kiln and sent to the forced air cooling chamber for forced convection cooling (quenching treatment). The cooling rate is controlled at 50℃ / min until room temperature. Finally, after being coarsely crushed by a jaw crusher, they are sent to an air jet mill for deagglomeration and pulverization. Powder with a particle size D90 of 18μm is collected to obtain rare earth composite energy health care products. Example 2:

[0051] This embodiment provides a method for preparing a rare earth composite energy health product based on synergy, including the following steps:

[0052] (1) Physical cost reduction and classification: After coarse crushing of natural monazite ore, it is continuously fed into a fluidized bed jet mill for ultrafine crushing. The pressure of the crushing air source is controlled at 0.7MPa; the dynamic air classifier at the top is turned on, the speed is set to 3800r / min, and the system induced draft is controlled at 20m³. 3 / min; collect light phase fine powder with an aerodynamic equivalent diameter D90≤10μm as raw material.

[0053] (2) Homogeneous mixing and porous molding: According to the mass fraction, 10 parts of the above-mentioned monazite fine powder, 78 parts of the aluminosilicate composite network forming agent obtained in Preparation Example 2, 8 parts of the in-situ reduction and network modifier obtained in Preparation Example 2, and 4 parts of industrial-grade urea powder as a pore-forming agent were weighed; the above dry powder materials were put into a V-type mixer, the speed was set to 20 r / min, and the dry mixing was carried out for 30 min; then transferred to a biaxial kneader, and deionized water accounting for 12% of the total mass of the dry powder materials was sprayed in evenly, and kneaded for 20 min to form mud; the mud was extruded and molded under a vacuum of -0.08 MPa using a vacuum extruder, cut into block blanks with a thickness of 75 mm, and naturally air-dried in an environment with a temperature of 25℃ and a relative humidity of 50% for 36 h.

[0054] (3) Atmosphere decoupling dynamic calcination: The dried billet is loaded into a refractory sagger and sent into a tunnel kiln for three-stage stepped calcination: First, it is kept at a constant temperature of 400℃ for 1.5h, and the kiln exhaust air makes the pore-forming agent completely decompose and form pores; then the billet is directly pushed into the high-temperature calcination zone that has been preheated to 1500℃, and high-purity argon gas with a purity of ≥99.9% is introduced as a protective atmosphere and the atmosphere is kept at a constant temperature for 1.0h, so that the magnesium powder is vaporized and thermal shock reduction occurs in the pores; then the argon gas is stopped at 1500℃, and high-temperature water vapor with a pressure of 0.35MPa is introduced, and the constant temperature calcination continues for 2.0h, so that the aluminosilicate forms a liquid phase and the pores collapse and solid solution occur.

[0055] (4) Quenching and deagglomeration restoration: The high-temperature clinker blocks that have been calcined are removed from the kiln and sent to the forced air cooling chamber for forced convection cooling (quenching treatment). The cooling rate is controlled at 75℃ / min until room temperature. Finally, after being coarsely crushed by a jaw crusher, they are sent to an air jet mill for deagglomeration and pulverization. Powder with a particle size D90 of 30μm is collected to obtain rare earth composite energy health care products. Example 3:

[0056] This embodiment provides a method for preparing a rare earth composite energy health product based on synergy, including the following steps:

[0057] (1) Physical cost reduction and classification: After coarse crushing of natural monazite ore, it is continuously fed into a fluidized bed jet mill for ultrafine crushing. The crushing air source pressure is controlled at 0.8MPa; the dynamic air classifier at the top is turned on, the speed is set to 4500r / min, and the system induced draft is controlled at 25m³. 3 / min; collect light phase fine powder with an aerodynamic equivalent diameter D90≤10μm as raw material.

[0058] (2) Homogeneous mixing and porous molding: According to the mass fraction, weigh 10 parts of the above-mentioned monazite fine powder, 80 parts of the aluminosilicate composite network forming agent obtained in Preparation Example 3, 10 parts of the in-situ reduction and network modifier obtained in Preparation Example 3, and 5 parts of ammonium carbonate powder as a pore-forming agent; put the above dry powder materials into a V-type mixer, set the speed to 25 r / min, and dry mix for 40 min; then transfer to a biaxial kneader, uniformly spray in 15% of the total mass of dry powder materials with deionized water, knead for 30 min to form mud; use a vacuum extruder to extrude and form under a vacuum of -0.09 MPa, cut into block blanks with a thickness of 100 mm, and air dry naturally in an environment with a temperature of 30℃ and a relative humidity of 60% for 48 h.

[0059] (3) Atmosphere decoupling dynamic calcination: The dried billet is loaded into a refractory sagger and sent into a tunnel kiln for three-stage stepped calcination: First, it is kept at a constant temperature of 500℃ for 2.5h, and the kiln exhaust air makes the pore-forming agent completely decompose and form pores; then the billet is directly pushed into the high-temperature calcination zone that has been preheated to 1550℃, and high-purity argon gas with a purity of ≥99.9% is introduced as a protective atmosphere and the atmosphere is kept at a constant temperature for 1.5h, so that the magnesium powder is vaporized and thermal shock reduction occurs in the pores; then the argon gas is stopped at 1550℃, and high-temperature water vapor with a pressure of 0.5MPa is introduced, and the constant temperature calcination continues for 3.0h, so that the aluminosilicate forms a liquid phase and the pores collapse and solid solution occur.

[0060] (4) Quenching and deagglomeration restoration: The high-temperature clinker blocks that have been roasted are removed from the kiln and sent to the forced air cooling chamber for forced convection cooling (quenching treatment). The cooling rate is controlled at 100℃ / min until room temperature. Finally, after being coarsely crushed by a jaw crusher, they are sent to an air jet mill for deagglomeration and pulverization. Powder with a particle size D90 of 48μm is collected to obtain rare earth composite energy health care products.

[0061] Comparative Examples 1-6:

[0062] Comparative Example 1:

[0063] Compared with Example 2, the difference is that fluidized bed airflow pulverization and kinetic classification were not used in step (1). Instead, the natural monazite ore was mechanically ball-milled and then forced to pass through a 1500-mesh dry vibrating screen for physical sieving to collect fine powder. All other steps are the same.

[0064] Comparative Example 2:

[0065] Compared with Example 2, the difference is that in step (3), atmosphere decoupling was not performed. Instead, after the billet was pushed into the high-temperature calcination zone at 1500°C, high-temperature steam at 0.35 MPa was directly introduced and maintained for 3.0 h, thus eliminating the protection and pure thermal shock reduction stage of introducing high-purity argon gas. All other steps are the same.

[0066] Comparative Example 3:

[0067] Compared with Example 2, the difference is that no pore-forming agent (industrial grade urea powder) is added to the formulation in step (2), and the thermal shock of directly pushing into the high-temperature zone is not used in step (3), but the temperature is slowly increased to 1500°C at a rate of 5°C / min. All other aspects are the same.

[0068] Comparative Example 4:

[0069] Compared with Example 2, the difference is that in step (3), only high-purity argon gas is introduced into the high-temperature roasting zone throughout the entire process (3.0h), and high-temperature water vapor is not switched to be introduced. All other aspects are the same.

[0070] Comparative Example 5:

[0071] Compared with Example 2, the difference is that in step (4), the high-temperature clinker block was not subjected to forced convection cooling (quenching treatment), but was naturally and slowly cooled to room temperature with the kiln. All other aspects are the same.

[0072] Comparative Example 6:

[0073] Compared with Example 2, the difference is that in step (2), when preparing the in-situ reduction and network modifier, no elemental magnesium powder is added; instead, an equal mass of light magnesium oxide is used. All other aspects are the same.

[0074] Test Case 1-6:

[0075] Test Example 1: Numerical Verification of the Physical Baseline Reduction Mechanism

[0076] Natural monazite ore, light phase fine powder collected after air classification in step (1) of Examples 1 to 3, and heavy phase coarse powder intercepted and discharged by the classifier wheel in the corresponding batch were taken as the test samples.

[0077] Each sample was dried at 105℃ to constant weight, and 500.0g was weighed and placed in a standard marin cup. The cup was sealed and left for 20 days to allow the nuclide to reach long-term radioactive equilibrium with its short half-life daughter.

[0078] The energy spectrum of the sample was measured using a high-purity germanium gamma spectrometer. The probe was placed in a low-background lead chamber, and the measurement time was set to 86,400 seconds to control statistical error.

[0079] Characteristic gamma-ray full-energy peaks of the 232Th and 238U decay series were selected, and the specific activities of 232Th and 238U in each sample were calculated, in units of Bq / kg. The test results were recorded after subtracting the environmental background count.

[0080] Table 1. Results of radioactivity specific activity tests on samples at each stage.

[0081]

[0082] The horizontal axis represents different batches of the embodiment, and the vertical axis uses a logarithmic scale to represent the specific activity value of radioactivity. By observing the difference in column height between the raw ore, light phase fine powder and heavy phase coarse powder within the same batch, the distribution and enrichment trend of radioactive materials in different phases can be visually displayed.

[0083] Conclusion: Combining the data in Table 1 and Figure 1 (Comparison of the specific activities of 232Th and 238U in different phases of natural monazite ore before and after airflow classification in Examples 1 to 3 of this invention) It can be seen that the specific activities of 232Th and 238U in natural monazite ore are at levels above 4700 Bq / kg and 1300 Bq / kg, respectively. Figure 1 In the figure, the vertical axis uses a logarithmic scale. The horizontal dashed line and dotted line represent the initial radioactivity specific activities of 232Th and 238U in the raw natural monazite ore before classification, respectively. After airflow classification in Examples 1 to 3, the specific activity of 232Th in the light phase fine powder collected for subsequent preparation decreased to 67.8-94.6 Bq / kg, and the specific activity of 238U decreased to 21.4-36.2 Bq / kg, a reduction of more than 97% of the original ore values, meeting the radioactivity exemption limits for common building materials and basic health care materials. Meanwhile, in the retained heavy phase coarse powder, the specific activities of the two nuclides showed an enrichment state several times that of the original ore. As... Figure 1 The difference in depth of the columnar particles represents the activity values ​​of different nuclides in the light phase fine powder and the heavy phase coarse powder after separation. As can be seen from the figure, the value of the light phase fine powder is much lower than the baseline of the original ore, while the value of the heavy phase coarse powder shows a clear enrichment transition.

[0084] The above data and spectral characteristics directly verify the physical trapping effect of fluid dynamics in the background reduction process, thus verifying the physical background reduction mechanism of this invention. Highly radioactive isotopes (Th, U) in monazite ore are not uniformly distributed within the main phosphate lattice, but rather exist primarily as independent mineral phases such as associated thorium or pitchblende. The true density of these enriched phases is greater than that of the main monazite crystalline phase. In the dynamically balanced flow field formed by fluidized bed airflow pulverization and the top classifying wheel, particles are simultaneously subjected to centrifugal force and air drag. Due to the high density of the associated heavy phases, they acquire greater centrifugal momentum under the same fluid dynamic conditions, are repelled to the periphery by the high-speed rotating classifying wheel, and fall back. The main crystalline phase, due to its lower density, has an aerodynamic equivalent diameter that meets the penetration condition and enters the collector with the airflow. Test results show that, without using chemical separation methods such as acid-base extraction, centrifugal fluid classification based solely on the density and aerodynamic differences between multiphase materials can effectively strip away radioactive heavy phases and control the background radiation value of the matrix material. The adjustment of parameters such as the speed of the stager wheel and the air volume (e.g., the higher speed in Example 3 corresponds to lower light phase radioactivity) further demonstrates the law that the physical interception effect is directly controlled by the flow field dynamic parameters.

[0085] Test Example 2: Macroscopic Property Verification of Liquid Phase Collapse Embedding Mechanism

[0086] In step (3) of Examples 1 to 3, at the end of the thermal shock reduction stage under a protective atmosphere but before water vapor is introduced, a portion of the billet is taken out and rapidly quenched with liquid nitrogen to retain its porous morphology, serving as an intermediate billet sample. At the same time, the material that has undergone constant temperature roasting with water vapor and subsequent forced convection cooling steps is collected as the final clinker sample.

[0087] Each sample was crushed and sieved to the required particle size. An appropriate amount of sample was placed in a test tube and degassed under vacuum at 200°C for 6 hours. Nitrogen adsorption and desorption tests were performed using a fully automated specific surface area and porosity analyzer at liquid nitrogen temperature. The specific surface area of ​​the sample was calculated based on BET theory, in m². 2 / g.

[0088] Samples of equal mass from each stage were laid flat in a sealed radon testing chamber. The background radon concentration in the testing chamber was controlled at 10 Bq / m³. 3 The following steps were performed: The sample chamber was sealed and allowed to stand for 24 hours. The cumulative change in radon concentration inside the chamber was continuously monitored using a radon meter. The radon release rate of the sample was calculated using the radon concentration change rate, sample surface area, and chamber volume parameters, in Bq / (m³). 2 ·s).

[0089] Table 2. Specific surface area and radon exhalation rate test results of samples at each stage.

[0090]

[0091] The horizontal axis is set as the example number and its corresponding two stages. The left Y-axis corresponds to the specific surface area value and is plotted as a bar chart, while the right Y-axis corresponds to the radon release rate value and is plotted as a scatter line chart. The difference in values ​​between the two stages within the same example demonstrates the synchronous relationship between specific surface area shrinkage and gas release inhibition.

[0092] Conclusion: Combining the data in Table 2 and Figure 2 (A line graph comparing the specific surface area and radon release rate of the materials in Examples 1 to 3 of this invention before steam mineralization (intermediate state billet) and after mineralization (final clinker) along the dual Y-axis.) It can be seen that the intermediate state billets in Examples 1 to 3 all exhibit high specific surface areas and radon release rates, with specific surface areas ranging from 26.83 to 41.67 m². 2 / g, radon release rate is 0.157 to 0.228 Bq / (m 2 ·s). In Figure 2 In the diagram, the Y-axis on the left corresponds to the specific surface area value, which is represented by a grouped bar chart. Light gray bars represent intermediate state billets, and dark gray bars represent final clinker. The Y-axis on the right corresponds to the radon precipitation rate value, which is represented by a scatter plot. Solid square scatter points represent intermediate state billets, and dashed triangular scatter points represent final clinker.

[0093] After being roasted with high-temperature steam, the specific surface area of ​​the clinker is reduced to 0.18 to 0.54 m². 2 / g, radon leaching rate decreased to 0.0016 to 0.0042 Bq / (m 2 After the phase change was completed by calcining with high-temperature steam, the column height and scattering position of the clinker decreased sharply. The specific surface area of ​​the material decreased by two orders of magnitude after the introduction of steam, and the rate of radon gas escape also decreased by two orders of magnitude. The synchronous shrinkage of this macroscopic data directly verifies the healing collapse effect of silicate liquid relative to the porous structure, as well as the resulting dense and airtight physical embedding effect, thus verifying the phase change effectiveness of the liquid phase collapse embedding mechanism.

[0094] Under the influence of pore-forming agent decomposition and high-pressure magnesium vapor diffusion, the intermediate-state billet forms an interconnected capillary network. The disintegration of the monazite lattice leads to the free states of nuclides such as Th and Ce, resulting in a large specific surface area and a high radon permeation diffusion rate. Upon introduction of high-temperature water vapor, water molecules penetrate the silicate lattice, polarizing and weakening the Si-O and Al-O bonds. With the fluxing effect of water vapor, basalt and alumina in the formulation produce an amorphous liquid phase. Driven by surface tension, the interconnected porous network collapses and heals, and free metal atoms, acting as network-modifying ions, dissolve into the amorphous three-dimensional aluminosilicate network. The material properties transform from a porous structure to a dense, gas-tight structure, and the specific surface area decreases. The liquid-phase solidification process cuts off the physical leakage path of gases, trapping radon and other gas atoms generated by radioactive decay within the mesoscopic network, thus achieving dense encapsulation of the radioactive source. The increase in temperature and water vapor pressure promoted the formation of the liquid phase and the network solid solubility, resulting in the final clinker of Example 3 having the smallest specific surface area and the lowest radon exudation rate.

[0095] Test Example 3: Comparison Test of Finished Product Safety Benchmarks

[0096] The powder products prepared in Examples 1 to 3, Comparative Example 1 and Comparative Example 4 were weighed out as test samples.

[0097] Each sample was placed in an infrared drying oven and dried at 85°C for 4 hours to remove surface adsorbed water. It was then removed and placed in a desiccator to cool to room temperature.

[0098] Accurately weigh each sample and spread it evenly in a special stainless steel measuring pan with a known base area. Compact the powder using a sample compactor to ensure the sample layer thickness is greater than or equal to the maximum saturation range of the measured radiation, and record the actual sample mass.

[0099] The prepared sample tray was transferred into the lead-shielded detection chamber of the low-background α / β measuring instrument. The measurement time for a single sample was set to 14400 seconds, and the instrument simultaneously recorded the count rates of total α and total β.

[0100] Under the same environmental and instrument parameters, the background count rate of the empty disk and the count rate of the known activity standard reference source were measured respectively. Based on the instrument calibration coefficient, the environmental background count value was subtracted, and the total alpha radioactivity and total beta radioactivity of each test sample were calculated, in units of Bq / kg, taking into account the sample mass and effective detection area.

[0101] Table 3. Results of total α and total β radioactivity specific activities for each powder product.

[0102]

[0103] The horizontal axis is set with different sample sources (Examples 1-3 and Comparative Examples 1 and 4), and the vertical axis uses a logarithmic scale to represent the specific activity values. Two sets of adjacent bars are used in the figure to represent the changes in total α and total β values, respectively. By comparing the column height differences between the comparative examples and the examples, the suppression effect of the process of the present invention on the radioactivity level of the finished product is visually displayed.

[0104] Conclusion: Combining the data in Table 3 and Figure 3 (Comparison of total α and total β radioactivity specific activities of the powder products prepared in Examples 1 to 3 of this invention with Comparative Examples 1 and 4) It can be seen that the total α radioactivity specific activity of the powder products prepared in Examples 1 to 3 is between 103.5 and 127.4 Bq / kg, and the total β radioactivity specific activity is between 261.9 and 312.6 Bq / kg. Figure 3 In the figure, the vertical axis uses a logarithmic scale, and the horizontal axis corresponds to different sample sources. In the two groups of bars in the figure, the light gray bars represent the total alpha radioactivity specific activity of the powder product, and the dark gray bars represent the total beta radioactivity specific activity. As can be seen from the figure, the bar heights of Examples 1 to 3 remain at a very low level at the bottom of the chart. These values ​​all meet the radioactivity exemption safety standards for conventional building and healthcare basic materials.

[0105] In contrast, Comparative Example 1, representing conventional physical sieving, and Comparative Example 4, which did not undergo water vapor encapsulation, showed a dramatic increase in column height, ranging from one to two orders of magnitude. The total α and total β specific activities of Comparative Example 1 reached 3841.2 Bq / kg and 5724.8 Bq / kg, respectively; the total α and total β specific activities of Comparative Example 4 also reached 865.3 Bq / kg and 1142.1 Bq / kg, exceeding the values ​​of the examples by several times. This dramatic difference in objective values ​​clearly highlights the decisive control effect of the present invention on the final safety benchmark of the product through a dual physical locking mechanism of front-end fluid dynamics interception and back-end amorphous network solid solution encapsulation.

[0106] In Comparative Example 1, conventional mechanical ball milling and physical sieving result in powder agglomeration and screen clogging during powder processing. Because the associated highly radioactive mineral phases have similar hardness to the main monazite crystal phase, effective separation cannot be achieved through single-particle-size screening. Therefore, all radioactive nuclides in the raw ore are retained in the final product, leading to excessive levels. In the embodiments of this invention, during the front-end processing stage, the physical property that the true density of the isotope-associated minerals (Th and U-enriched phases) is greater than that of the main monazite crystal phase is utilized. High-density particles are forcibly repelled by centrifugal force in a fluidized bed aerodynamic equilibrium field, thereby eliminating most of the radioactive background material at the source.

[0107] In Comparative Example 4, without the introduction of a steam mineralization stage, the silicate liquid phase was not fully generated, and the material retained numerous porous channels created by the pore-forming agent and magnesothermic reduction. During subsequent deagglomeration and pulverization into powder, microscopic free nuclides not embedded in the amorphous network were exposed on the powder surface. Combined with the release of residual radioactive decay products within the internal pores, this led to a rise in the radioactivity level of the finished product. In the embodiments of this invention, steam is introduced as a flux in the downstream calcination stage, polarizing and weakening the silicon-oxygen and aluminum-oxygen bonds to form a high-viscosity amorphous liquid phase. Driven by surface tension, free Th and Ce metal atoms, acting as network-modifying ions, dissolve into the amorphous three-dimensional network of aluminosilicates through strong covalent and ionic bonds. The physical collapse of the pores seals the decaying nuclides within the dense network. Even after final physical pulverization into micron-sized powder, the radioactive material remains bound within the crystal lattice and glass phase. Data comparison between the two processes confirms the necessity and synergistic effect of the background reduction and network encapsulation mechanism in ensuring product safety.

[0108] Test Example 4: Comparative Test of Life Light Wave Energy Release

[0109] The powder products prepared in Examples 1 to 3, Comparative Examples 3, 5 and 6 were weighed out and used as test samples.

[0110] Each powder sample was placed into a cemented carbide mold, and an axial pressure of 30 MPa was applied on a powder press for 2 minutes to compress a dense circular sample with a diameter of 50 mm and a thickness of 3 mm. The surface of the circular sample was ensured to be flat and free of cracks.

[0111] Turn on the Fourier transform infrared spectrometer and the external normal emissivity test accessory. Set the ambient temperature to a constant 20°C and the relative humidity to below 45%. Calibrate the instrument's radiation energy baseline using a standard blackbody cavity at 36°C.

[0112] The pressed circular sample was placed on a constant-temperature test bench, and the surface temperature of the sample was brought to and stabilized at 36℃. The radiation spectrum of the sample surface was scanned using a spectrometer, and the infrared radiation energy of the sample in the 8 to 10 μm band was collected. The ratio of the sample radiation energy to the blackbody radiation energy at the same temperature was calculated to obtain the normal total emissivity in the 8 to 10 μm band, and the result was expressed as a percentage.

[0113] Table 4. Test results of normal total emissivity of each powder product in the 8 to 10 μm wavelength band.

[0114]

[0115] The horizontal axis represents different sample sources (including Examples 1 to 3 and Comparative Examples 3, 5, and 6), and the vertical axis represents the percentage value of normal total emissivity. All columns are filled with a uniform grayscale. The difference in column height visually demonstrates the impact of different preparation processes on the far-infrared radiation properties of the powder material.

[0116] Conclusion: Combining the data in Table 4 and Figure 4 (A bar chart comparing the normal total emissivity of the powder products prepared in Examples 1 to 3 of this invention with Comparative Examples 3, 5, and 6 in the 8 to 10 μm core band) It can be seen that the normal total emissivity of the powder products in Examples 1 to 3 in the 8 to 10 μm band ranges from 91.5% to 94.1%. Figure 4 In the figure, the vertical axis represents the percentage of normal total emissivity, and the horizontal axis corresponds to different sample sources. Gray-scale bars are used to represent the test results for each sample, with the specific emissivity value directly labeled above the bars. As can be seen from the figure, the values ​​for Examples 1 to 3 consistently remain above 90%.

[0117] In comparison, the normal total emissivity of Comparative Example 3 was 75.4%, that of Comparative Example 5 was 72.9%, and that of Comparative Example 6 was 63.7%. As shown in the figure, the height of the column decreases in a step-like manner. The values ​​of Comparative Example 3 (which did not undergo thermal shock crystallization), Comparative Example 5 (which underwent defect healing through slow cooling), and Comparative Example 6 (which did not involve strong reduction of magnesium powder) were all lower than those of the examples.

[0118] The far-infrared emission capability of monazite matrix and composite silicate materials depends on the dipole moment variation and phonon resonance transition effect within the microcrystalline lattice. In the formulation system of Comparative Example 6, the absence of magnesium powder for high-temperature reduction resulted in the absence of heterovalent substitution of transition metal elements and generation of oxygen vacancy defects within the material lattice. The lattice structure maintained a long-range order and a highly symmetrical state, leading to insufficient intrinsic excitation sources for infrared radiation and a normal total emissivity of only 63.7%.

[0119] Comparative Example 3 did not undergo a thermal shock stage during its preparation. Under slow heating conditions, the magnesium powder underwent conventional oxidation or melting, failing to instantaneously transform into high-pressure magnesium vapor. The monazite lattice was not damaged by the internal mechanical stress generated by the instantaneous expansion of the high-pressure gas, and the crystal structure did not experience in-situ physical fracture. The low degree of microstructural decomposition in the material limited its absorption and emission conversion efficiency for infrared thermal energy, resulting in a decrease in the normal total emissivity to 75.4%.

[0120] Comparative Example 5 employed a natural, slow cooling method. The oxygen vacancies, dislocations, and lattice distortions generated by the pore-forming reaction and reduction process during the high-temperature stage gained relaxation time during cooling. Microscopic lattice defects underwent thermodynamic healing, and atoms rearranged to a low-energy, stable symmetry state, leading to the disappearance of asymmetric polarization centers within the crystal. The weakening of dipole moment fluctuations reduced the electron-phonon coupling resonant transition effect in the infrared band, decreasing the normal total emissivity to 72.9%.

[0121] The process flow of Examples 1 to 3 integrates strong reduction of magnesium powder, in-situ crystal breaking through instantaneous thermal shock, and forced air-cooling quenching. Strong reduction induces lattice defects and heterovalent substitution; instantaneous high temperature causes magnesium to rapidly vaporize, triggering physical expansion and rupture of the lattice, disrupting the material's long-range microscopic order; subsequent forced air-cooling quenching forcibly cuts off the thermal diffusion paths of atoms, freezing and fixing the asymmetric polarized microregions and lattice defects formed at high temperature within the room-temperature structure. The coexistence of multiple defects breaks the original symmetry bandgap, increasing infrared-active vibrational modes, enabling the material to convert thermal energy into infrared radiation energy in the 8-10 μm wavelength range. The above physical test values ​​directly demonstrate the role of the specific forced air-cooling quenching and in-situ crystal breaking steps in the process of this invention in activating and maintaining the material's far-infrared emission capability.

[0122] Test Example 5: Comparative Test of Lattice Defect Activation Effect

[0123] The powder products prepared in Examples 1 to 3, Comparative Example 5, and Comparative Example 6 were weighed as test samples. Each powder sample was placed into a mold and pressed into a circular sample with a diameter of 20 mm and a thickness of 1 mm under a pressure of 20 MPa. Conductive silver paste was uniformly coated on both the upper and lower surfaces of the sample and cured at 80°C to form an electrode.

[0124] The prepared sample was fixed on an insulated test bench equipped with a temperature control module, and the entire sample was placed in an electromagnetically shielded anechoic chamber to isolate it from interference from stray electromagnetic signals. The electrodes at both ends of the sample were connected to a high-precision picoammeter via wires.

[0125] The initial reference temperature of the test bench was set to 36.0℃. After the system reached thermal equilibrium and the static charge was released, periodic temperature disturbances were applied to the sample through the temperature control module. The temperature disturbance mode was set to a triangular wave with a fluctuation range of 34.5℃ to 37.5℃, and the heating and cooling rate was controlled at 0.1℃ / s to simulate the minute temperature fluctuations that occur when human skin comes into contact with the material.

[0126] Under continuous temperature cycle perturbation, the picoampere synchronously acquires the short-circuit thermal shock current signal in the closed loop. Polarization microcurrent data are recorded over five consecutive temperature cycles. The absolute values ​​of the positive and negative microcurrent peaks generated during the heating and cooling phases in each cycle are extracted, and the average value is calculated as the peak polarization microcurrent of the sample, expressed in picoamperes (pA).

[0127] Table 5. Peak polarization microcurrent test results of each powder product under temperature disturbance

[0128]

[0129] The horizontal axis represents different sample sources (including Examples 1 to 3 and Comparative Examples 5 and 6), and the vertical axis represents the peak value of the polarization microcurrent, in pA. All columns are filled with a uniform grayscale. The significant difference in column height between the examples and comparative examples visually demonstrates the influence of different preparation processes on the concentration of spontaneously polarized microregions within the powder material.

[0130] Conclusion: Combining the data in Table 5 and Figure 5 (A bar chart comparing the peak polarization microcurrent of the powder products prepared in Examples 1 to 3 of this invention with those in Comparative Examples 5 and 6 under temperature disturbance) shows that Examples 1 to 3, under an environment simulating small temperature cyclic disturbances in the human body (34.5℃ to 37.5℃), can generate a response microcurrent in the range of one hundred to two hundred picoamperes, with the peak polarization microcurrent between 185.6 and 264.3 pA. Figure 5 In the figure, the vertical axis represents the magnitude of the polarization microcurrent peak value, in pA; the horizontal axis corresponds to different sample sources. Gray-scale bars are used uniformly to represent the test results for each sample, with the specific current peak value labeled above the bars.

[0131] In contrast, Comparative Example 5, which underwent slow cooling to eliminate defects, had a peak polarization current of 24.1 pA; while Comparative Example 6, which did not use magnesium powder to induce oxygen vacancies, had a peak polarization current of only 11.5 pA. Figure 5 As shown, the height of the columns in these two comparative examples drops precipitously, and the measured microcurrent values ​​remain only at the baseline level. The current values ​​in the embodiment are more than an order of magnitude higher than those in the comparative examples.

[0132] The phenomenon of microcurrents generated by materials under temperature changes originates from the pyroelectric effect, and its underlying physical basis depends on the presence of non-centrosymmetric spontaneous polarization centers within the material's crystal lattice. In Comparative Example 6, no magnesium powder was added to the formulation, and the material did not undergo a reduction reaction during the high-temperature calcination stage. No heterovalent substitution of transition metal elements occurred in the main crystal phase, and no oxygen vacancy defects were generated. The material's crystal lattice maintained a centrosymmetric structure, lacking spontaneously polarized microregions, and therefore could not generate polarization charge displacement under temperature perturbations, resulting in the lowest measured microcurrent value.

[0133] Comparative Example 5 exhibited lattice defects at high temperatures, but employed a natural, slow cooling method. During the relaxation process of slow cooling, driven by thermodynamics, oxygen vacancies, dislocations, and lattice distortions formed at high temperatures healed, atoms rearranged to lower energies, and the lattice symmetry was restored. The concentration of internal polarized microregions decreased, causing the thermally excited polarization current to drop back to 24.1 pA.

[0134] Examples 1 to 3 involve inducing oxygen vacancies and heterovalent substitution through strong reduction of magnesium powder, followed by forced air cooling quenching after vaporization and crystal breaking. Forced air cooling quenching blocks the thermal diffusion healing path of lattice defects, freezing and retaining high concentrations of non-equilibrium defects and non-centrosymmetric polarized microregions within the room-temperature material. Under temperature disturbances simulating human body temperature fluctuations, the lattice parameters within these solidified polarized microregions undergo thermal expansion and contraction, resulting in periodic changes in spontaneous dipole moments. These dipole moment disturbances disrupt the charge balance on the sample surface, driving surface-bound charges to migrate through an external circuit, forming a polarized microcurrent at the picoampere level. The aforementioned macroscopic electrical test values ​​objectively verify that the forced air cooling quenching process of this invention freezes and retains a large number of spontaneously polarized microregions within the material, demonstrating the activation and retention effect of forced air cooling quenching on lattice defects, and simultaneously confirming the underlying physical basis for the resonance between the product and an external micro-heat source, generating a thermally excited current.

[0135] Test Example 6: Comparative Test of Spatial Micro-Electric Field Effects

[0136] Weigh equal masses of the powder products prepared in Examples 1 to 3 and Comparative Examples 1, 3, 4, 5, and 6 as test samples. Spread each sample evenly in a glass petri dish of fixed diameter, ensuring uniform thickness and surface area.

[0137] Prepare an acrylic dynamic sealed test chamber with an internal volume of 1 cubic meter. The chamber is equipped with a temperature and humidity control system and a DC micro fan. Adjust the environmental parameters inside the test chamber, setting the temperature to 25℃ and the relative humidity to 60%. Record the initial background concentration of negative oxygen ions in the chamber air.

[0138] Place the glass petri dish containing the sample on the stage in the center of the test chamber. Close the sealed door of the test chamber. Turn on the miniature fan and set the wind speed to 1.0 m / s to maintain micro-circulation of air inside the chamber.

[0139] The test chamber was run for 120 minutes to allow the concentration of negative oxygen ions to reach a dynamic equilibrium. A capacitive air ion meter was used to collect negative oxygen ion concentration data at a position 30 cm above the stage. Measurements were taken continuously for 30 minutes, with data recorded every minute. The arithmetic mean of the 30 data sets was calculated as the negative oxygen ion release concentration of the test sample, expressed in ions / cm³. 3 .

[0140] After each test, the chamber's exhaust system is activated. Clean air is then introduced to flush the test chamber. Once the concentration of negative oxygen ions inside the chamber returns to its initial background level, the next set of samples is placed inside for testing.

[0141] Table 6. Test results of negative oxygen ion release concentration of each powder product.

[0142]

[0143] The horizontal axis represents Examples 1 to 3 and Comparative Examples 1, 3, 4, 5, and 6, and the vertical axis represents the concentration of negative oxygen ions released, in units of ions / cm³. 3 Each column is filled with a uniform pure gray, and the edge lines are set to black. The differences in column height distribution in the figure demonstrate the comprehensive impact of different preparation process combinations on the negative oxygen ion release performance of the powder product.

[0144] Conclusion: Combining the data in Table 6 and Figure 6 (A bar chart comparing the negative oxygen ion release concentration of the powder products prepared in Examples 1 to 3 of this invention with that of Comparative Examples 1, 3, 4, 5, and 6 in a dynamic sealed chamber) It can be seen that the negative oxygen ion release concentration of the powder products prepared in Examples 1 to 3 in the dynamic sealed chamber ranges from 4987 to 6125 ions / cm³. 3 Between. Figure 6 In the figure, the vertical axis represents the concentration of negative oxygen ions released, with the unit being ions / cm³. 3 The horizontal axis corresponds to different sample sources. Gray bars are used uniformly in the figure to represent the macroscopic test results of each sample, with the specific release concentration value marked above the bar. As can be seen from the figure, the negative oxygen ion release concentrations of Examples 1 to 3 range from 4900 to 6200 ions / cm³. 3 The range.

[0145] In contrast, the column heights of the various comparative examples showed varying degrees of reduction. Comparative Example 1 had a negative oxygen ion release concentration of 2451 ions / cm³. 3 The concentration of negative oxygen ions released in Comparative Example 4 was 1894 ions / cm³. 3 Comparative Example 1, relying on conventional radioactive radiation alone, and Comparative Example 4, which did not form a physically closed micro-electric field, had values ​​remaining around 2,000; while Comparative Example 3, lacking in-situ crystal breaking, had values ​​of 1356 ions / cm. 3 Comparative Example 5 (1103 ions / cm) showed that natural slow cooling eliminated defects. 3 ) and Comparative Example 6 (684 ions / cm) without reduction defects. 3 ), and its concentration value further dropped to an extremely low level.

[0146] The generation of negative oxygen ions in the air depends on the ionization of gas molecules (water and oxygen molecules) in the air. Comparative Example 1 retains the associated radioactive nuclides in the original ore and possesses high radioactivity specific activity. Radiation collisions with air molecules trigger ionization. The powder has not undergone microscopic lattice modification and specific surface area expansion, lacking the synergistic effect of multiple physical fields, thus limiting ionization efficiency, and the negative oxygen ion concentration remains at 2451 ions / cm³. 3 .

[0147] In Comparative Example 6, the system did not introduce strong reduction effects from magnesium powder, and no oxygen vacancies or transition metal heterovalent substitution centers were generated within the crystal lattice, maintaining centrosymmetry. The material lacks polarizable microregions, thus failing to generate a pyroelectric microfield. It exhibits low far-infrared emissivity, indicating that water molecules are not resonantly activated. The number of gas molecules ionized under physical adsorption is low, with a negative oxygen ion release concentration of 684 ions / cm³. 3 .

[0148] Comparative Example 5 employed a natural slow cooling process. The oxygen vacancies and lattice distortions formed during high-temperature calcination underwent thermodynamic healing during cooling. A large number of internal polarized micro-regions disappeared, and the surface micro-electric field effect weakened, making it impossible to effectively electrolyze adsorbed water molecules on the surface using electrostatic high voltage. The measured value dropped to 1103 ions / cm³. 3 .

[0149] Comparative Example 3 was not subjected to instantaneous thermal shock treatment. The monazite lattice was not damaged by the internal mechanical stress generated by vaporization expansion, and the crystal structure did not undergo physical fracture. The powder product had a low specific surface area and a small number of exposed polarized micro-regions. The reduction in the gas-solid contact area limited the coverage of the surface electric field on air molecules, and the negative oxygen ion concentration was measured at 1356 ions / cm³. 3 .

[0150] Comparative Example 4 lacked the water vapor encapsulation process, and no amorphous aluminosilicate network was formed. The internal structure was not physically locked, the microscopic charge conduction pathways were interrupted, and a uniform and continuous spatial micro-electric field could not be formed on the material surface. The efficiency of water molecule electrolysis decreased, and the concentration of negative oxygen ions released was 1894 ions / cm³. 3 .

[0151] The microstructures of Examples 1 to 3 retain extremely low doses of radionuclides, active lattice defects, and non-centrosymmetric polarized microregions. Trace background radioactivity emits radiation, providing the initial activation energy required to excite air molecules. High far-infrared emission causes water molecules adsorbed on the material surface to undergo dipole resonance, reducing their ionization potential. Under slight temperature fluctuations and airflow disturbances in the test environment, the polarized microregions solidified on the powder surface undergo pyroelectric response, forming a polarized microcurrent and a high-voltage electrostatic region (spatial micro-electric field) on the material surface. Water molecules activated by far-infrared resonance undergo electrolysis under the influence of the spatial micro-electric field, dissociating into hydrogen ions and hydroxide ions. The stripped electrons are captured by oxygen molecules in the air, combining to generate negative oxygen ions. Comprehensive comparative data demonstrates that the efficient induction of negative oxygen ion release by the material is not due to a single characteristic, but rather relies on the synergistic effect of three physical factors: extremely low background radiation, high far-infrared emission, and the pyroelectric micro-electric field. This verifies the necessity and overall technical advantages of the multi-step combination scheme in this preparation process in activating the spatial ionization performance of the product. The strong reduction defect creation, in-situ crystal breaking, and ultra-cold quenching steps in the preparation scheme have an interdependent physical relationship in activating multiple energy releases.

Claims

1. A rare earth composite energy health product based on synergy, characterized in that, The synergistic rare earth composite energy health product is made from the following raw materials by weight through mixing, roasting, and polymerization: Fine powder of Solanum monophylla: 10 parts; Aluminosilicate composite network forming agent: 75-80 parts; In-situ reduction and network modifier: 5-10 parts; Pore-forming agent: 3-5 parts.

2. The rare earth composite energy health product according to claim 1, characterized in that, The raw material consists of the following components in parts by weight: 10 parts of fine powdered monolith; 78 parts of aluminosilicate composite network forming agent; 8 parts of in-situ reduction and network modifier; Four parts of pore-forming agent.

3. The rare earth composite energy health product according to claim 1, characterized in that, The aluminosilicate composite network forming agent is an inorganic mineral powder mixture, which is composed of microporous basalt-type volcanic rock or andesite-type volcanic rock, hematite-type ochre, porphyritic andesite-type maifanite, and alum-type alum, and the mass ratio of the microporous basalt-type volcanic rock or andesite-type volcanic rock, the hematite-type ochre, the porphyritic andesite-type maifanite, and the alum-type alum is (35-40):(10-15):(15-16):(10-15).

4. The rare earth composite energy health product according to claim 1, characterized in that, The in-situ reduction and network modifier is composed of metallic magnesium powder and light magnesium oxide, and the mass ratio of metallic magnesium powder to light magnesium oxide is 1:1 to 1:

2. The magnesium powder has a purity greater than 99.0% and a particle size of 200-300 mesh.

5. The rare earth composite energy health product according to claim 1, characterized in that, The pore-forming agent is industrial-grade urea powder or ammonium carbonate powder. The monazite fine powder is a natural monazite light phase fine powder with an aerodynamic equivalent diameter D90 ≤ 10 μm.

6. A method for preparing a rare earth composite energy health product based on synergy as described in any one of claims 1-5, characterized in that, Includes the following steps: Natural monazite ore is coarsely crushed and then subjected to airflow ultrafine grinding and dynamic classification to collect light phase fine powder as the monazite fine powder raw material. The monazite fine powder, aluminosilicate composite network forming agent, in-situ reducing and network modifying agent and pore-forming agent are dry-mixed evenly to obtain dry powder material, which is then sprayed with deionized water and kneaded to form mud. After vacuum extrusion molding, cutting and natural air drying, block blanks are obtained. The block-shaped billet is loaded into a kiln and subjected to three-stage stepped firing, which proceeds in sequence as follows: low-temperature exhaust to decompose the pore-forming agent, firing under a high-temperature inert protective atmosphere, and firing under a high-temperature steam atmosphere to obtain high-temperature clinker blocks. The high-temperature clinker blocks are removed from the kiln and subjected to forced air cooling to room temperature. Finally, they are crushed, deagglomerated and pulverized by air jet milling, and the powder is collected to obtain the rare earth composite energy health care product based on synergy.

7. The preparation method according to claim 6, characterized in that, The process parameters for airflow ultrafine grinding and dynamic classification are as follows: The process is carried out in a fluidized bed jet mill, with the grinding gas source pressure controlled at 0.6-0.8 MPa. The dynamic airflow stager speed is set to 3000-4500 r / min, and the system induced draft volume is controlled at 15-25 m³ / min. 3 / min.

8. The preparation method according to claim 6, characterized in that, The amount of deionized water injected accounts for 10%-15% of the total mass of the dry powder material; The vacuum degree of the vacuum extrusion molding is -0.06MPa to -0.09MPa; The environmental conditions for natural air drying are: temperature 20-30℃, relative humidity 40%-60%, and air drying time 24-48h.

9. The preparation method according to claim 6, characterized in that, The specific process conditions for the three-stage stepped roasting are as follows: First stage: Maintain a constant temperature of 300-500℃ for 1.0-2.5 hours; Second stage: Proceed to the high-temperature roasting zone preheated to 1450-1550℃, and introduce nitrogen or argon gas with a purity ≥99.9% as a protective atmosphere, and maintain the temperature for 0.5-1.5 hours; Third stage: Stop the protective atmosphere at 1450-1550℃, switch to high-temperature steam at a pressure of 0.2-0.5MPa, and continue constant temperature roasting for 1.5-3.0h.

10. The preparation method according to claim 6, characterized in that, The cooling rate of the forced air cooling treatment is controlled at 50-100℃ / min; The particle size D90 of the collected powder is controlled to be 18-48 μm.

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