阅读说明：本技术 一种硅格位掺杂竞争发光中心的稀土正硅酸盐闪烁材料及其制备方法和应用 (Rare earth orthosilicate scintillation material with silicon lattice doped competitive luminescence center and preparation method and application thereof ) 是由 丁栋舟 赵书文 万博 施俊杰 陈露 袁晨 王林伟 于 2020-11-16 设计创作，主要内容包括：本发明涉及一种硅格位掺杂竞争发光中心的稀土正硅酸盐闪烁材料及其制备方法和应用,所述硅格位掺杂竞争发光中心的稀土正硅酸盐闪烁材料的化学式为RE-(2(1-x))Ce-(2x)Si-(1-y)M-yO-5；其中RE为稀土离子；M为占据硅格位的第二发光中心,选自钛Ti、铬Cr、锰Mn、钴Co中至少一种；0＜x≤0.05,0＜y≤0.1。(The invention relates to a rare earth orthosilicate scintillator with silicon lattice doped competitive luminescence centerThe chemical formula of the rare earth orthosilicate scintillation material with silicon lattice doped competitive luminescence center is RE 2(1‑x) Ce 2x Si 1‑y M y O 5 (ii) a Wherein RE is a rare earth ion; m is a second luminescence center occupying silicon lattice sites and is selected from at least one of titanium Ti, chromium Cr, manganese Mn and cobalt Co; x is more than 0 and less than or equal to 0.05, and y is more than 0 and less than or equal to 0.1.)

1. The rare earth orthosilicate scintillation material with the silicon lattice doped competitive luminescence center is characterized in that the chemical formula of the rare earth orthosilicate scintillation material with the silicon lattice doped competitive luminescence center is RE_2(1-x)Ce_2xSi_1-yM_yO₅(ii) a Wherein RE is a rare earth ion; m is a second luminescence center occupying silicon lattice sites and is selected from at least one of titanium Ti, chromium Cr, manganese Mn and cobalt Co; x is more than 0 and less than or equal to 0.05, and y is more than 0 and less than or equal to 0.1.

2. The rare earth orthosilicate scintillator material according to claim 1, wherein said RE is selected from at least one of lanthanum La, cerium Ce, praseodymium Pr, neodymium Nd, promethium Pm, samarium Sm, europium Eu, gadolinium Gd, terbium Tb, dysprosium Dy, holmium Ho, erbium Er, thulium Tm, ytterbium Yb, lutetium Lu, scandium Sc, yttrium Y, preferably at least one of Lu, Y, Gd, La.

3. The rare earth orthosilicate scintillation material according to claim 1 or 2, wherein the rare earth orthosilicate scintillation material with silicon lattice site doped competition luminescent centers is further added with other doping elements A, and the chemical formula is RE_2(1-x-a)Ce_2xA_2aSi_1-yM_yO₅A is more than 0 and less than or equal to 0.01; the other doping element A is at least one selected from Li, Na, K, Rb, Cs, Mg, Ca, Sr, Sc and Cu.

4. Rare earth orthosilicate scintillation material according to any one of claims 1-3, wherein the rare earth orthosilicate scintillation material with silicon lattice doping competing luminescent centers is a rare earth orthosilicate scintillation polycrystalline powder with silicon lattice doping competing luminescent centers, a rare earth orthosilicate scintillation ceramic with silicon lattice doping competing luminescent centers, or a rare earth orthosilicate scintillation single crystal with silicon lattice doping competing luminescent centers.

5. A preparation method of rare earth orthosilicate scintillation polycrystalline powder with silicon lattice doped competitive luminescence center is characterized by comprising the following steps:

(1) weighing at least one of oxide and carbonate of A, oxide of M, CeO and/or rare earth orthosilicate scintillation polycrystalline powder with silicon lattice doped with competitive luminescence center₂ 、SiO₂And oxide of RE and mixingTo obtain mixed powder;

(2) and carrying out solid phase reaction on the obtained mixed powder at 1000-2000 ℃ for 5-200 hours to obtain cerium co-doped orthosilicate scintillation polycrystalline powder.

6. A preparation method of rare earth orthosilicate scintillating ceramic with silicon lattice doped competitive luminescence center is characterized by comprising the following steps:

(1) weighing at least one of oxide A and carbonate A, oxide M and CeO according to the chemical formula of the rare earth orthosilicate scintillation ceramic with silicon lattice doped competitive luminescence center₂ 、SiO₂Mixing with RE oxide to obtain mixed powder;

(2) pressing the obtained mixed powder, and carrying out solid phase reaction for 5-200 hours at 1000-2000 ℃ to obtain cerium co-doped orthosilicate scintillating ceramic; preferably, the pressure for the press molding is 0.03GPa to 5 GPa.

7. A preparation method of a rare earth orthosilicate scintillation single crystal with silicon lattice doped competitive luminescence center is characterized by comprising the following steps:

(1) weighing at least one of oxide A and carbonate A, oxide M and CeO according to the chemical formula of the rare earth orthosilicate scintillation ceramic with silicon lattice doped competitive luminescence center₂ 、SiO₂Mixing with RE oxide to obtain mixed powder;

(2) heating the obtained mixed powder to be molten, and growing the rare earth orthosilicate scintillation single crystal with the silicon lattice doped competition luminescence center by adopting a pulling method, a Bridgman method, a temperature gradient method, a heat exchange method, a kyropoulos method, a top seed crystal method, a fluxing agent crystal growth method or a micro-pulling down method.

8. The application of the rare earth orthosilicate scintillation ceramic with silicon lattice doped competitive luminescence center and the rare earth orthosilicate scintillation single crystal with silicon lattice doped competitive luminescence center in the fields of high-energy physical detection and particle discrimination and fast nuclear medical imaging is provided.

Technical Field

The invention relates to a method for regulating and controlling the performance of a rare earth orthosilicate scintillation material by a competitive luminescence mechanism and application thereof, belonging to the technical field of scintillation materials.

Background

An inorganic scintillating material is a crystalline energy converter that converts the energy of high-energy photons (X/gamma rays) or particles (protons, neutrons, etc.) into easily detectable ultraviolet/visible photons. Detectors made of inorganic scintillation crystals are widely used in the fields of high-energy physics, nuclear physics, space physics, nuclear medicine diagnosis (XCT, PET), geological exploration, safety inspection and the like. With the rapid development of nuclear detection and related technologies, higher requirements are put forward on the performance of scintillation crystals, the conventional scintillation crystals such as nai (tl), BGO, PWO and the like cannot meet the application requirements, and the aluminate and silicate scintillation crystals of the new generation gradually become research hotspots due to the characteristics of high light output, rapid attenuation and the like.

With rare earth ions Ce³⁺As an activator, use is made of Ce³⁺5d → 4f YuzhiyuThe transition is allowed to obtain high-intensity fast decay luminescence, such as: YAG, GAGG, LYSO, GSO, YAP, LuAP and the like are emerging as a new class of scintillating materials. And conventional NaI Tl, BGO, BaF₂Compared with PWO inorganic scintillation crystals, Ce ion doped high temperature oxide crystals have both high light output (about 2-10 times of BGO crystals) and fast decay (about 1/5-1/20 of BGO crystals), so that the scintillation crystals with excellent performance are highly regarded by the scientific community. The Ce ion doped rare earth orthosilicate has the characteristics of high light output, fast luminescence attenuation, many effective atomic numbers, large density and the like, and is a scintillation material with excellent performance. However, the field of high-energy physical and nuclear medical imaging puts higher demands on its temporal characteristics. In high-energy physical application, the type of particles can be distinguished through the energy of the particles, the energy of the particles corresponds to the scintillation rise time behavior, and the shorter the rise time of the scintillation material per se is, the stronger the capability of distinguishing the particles is; in the field of nuclear medicine imaging, image resolution, scan speed, signal-to-noise ratio, and radiation dose are all closely related to the rise and decay times of the scintillation material. The use of time-of-flight (TOF) techniques in Positron Emission Tomography (PET), which is the direction of development in future nuclear medicine imaging, allows the location of events to be limited to a small range, reducing the number of voxels involved in the reconstruction of events, leading to an increase in local information concentration. TOF technology has high requirements on the rise time and the decay time of the scintillation material, and the time resolution CTR ∞ (rise time multiplied by decay time ÷ light yield)^0.5The magnitude of 10ps is reached, the sensitivity of PET is improved by at least 16 times, and the space-time resolution of PET molecular imaging is improved to the maximum extent; meanwhile, the radiation dose of the molecular imaging program can be reduced to a negligible low level, the synthesis amount of the radiopharmaceutical required by each examination is reduced, the diagnosis of cardiovascular diseases, nervous diseases, metabolism, inflammation, infectious diseases or metabolic diseases (such as diabetes) by molecular imaging is further expanded, and the detection objects comprise pediatrics, neonates and prenatal department without the need of carrying out full-angle scanning on patients. The CTR of the current commercial PET is 500-250ps, the new generation Ce ion doped rare earth orthosilicate scintillation material is expected to reduce the CTR to be less than 100ps, and in order to move to the target of 10ps, the CTR needs to be further reducedThe time characteristic of the rare earth orthosilicate scintillation material is shortened. At present, for a Ce ion doped rare earth orthosilicate scintillation system, relevant literature focuses on Ce³⁺And regulating and controlling the rare earth lattice site and the anion lattice site of oxygen. For example, co-doping effects of Mg, Ca and Tb in LSO: Ce are reported, and co-doping of 0.2 at.% Ca is found to improve the light output of the crystal, and the co-doping of Ca leads to an increase in the content of Ce1 in LSO: Ce. Patent 1 (chinese publication No. CN108059957A) discloses that doping rare earth lattice sites with Ca or Mg and co-doping oxygen sites with F or Cl anions can increase the light output of orthosilicate and reduce afterglow. Patent 2 (Chinese publication No. CN108139492A) discloses the disclosure of₂SiO₅The doping of Ti, Cr, Mn, Co elements in the a-site of the silicate scintillator material enables non-radiative energy transfer to take off part of the energy from the excited luminescence center, resulting in a significant reduction in the duration of the dominant amplitude component of the scintillation response. However, at present, no report is found on the doping of silicon sites of pure rare earth orthosilicate scintillating materials.

Disclosure of Invention

According to the actual application needs and the realization of the purpose, the invention aims to provide a method for regulating and controlling the performance of a rare earth orthosilicate scintillation material by a competitive luminescence mechanism and application thereof, create a new scintillation material with high light yield and ultra-fast luminescence performance, and better meet the use requirements of high-energy physical detection and particle discrimination and fast nuclear medicine imaging (TOF-PET, PET-CT and PET-MRI).

In a first aspect, the invention provides a silicon-lattice-doped competitive luminescence center rare earth orthosilicate scintillation material, and the chemical formula of the silicon-lattice-doped competitive luminescence center rare earth orthosilicate scintillation material is RE_2(1-x)Ce_2xSi_{1- y}M_yO₅(ii) a Wherein RE is a rare earth ion; m is a second luminescence center occupying silicon lattice sites and is selected from at least one of titanium Ti, chromium Cr, manganese Mn and cobalt Co; x is more than 0 and less than or equal to 0.05, and y is more than 0 and less than or equal to 0.1.

Most of the doped ions studied at present are optically inert, and no consideration has been given to improving the temporal behavior by using the competitive mechanism generated by the second activation center, even if any, limited to rare earthAnd doping the lattice site. The inventor finds that silicon and oxygen form SiO in the rare earth orthosilicate scintillation material₄]The doping of the silicon lattice sites can indirectly influence the activation centers on the rare earth lattice sites through oxygen ions and oxygen vacancies, the fact that the silicon lattice site doping competition luminescent centers of the rare earth orthosilicate scintillation material is significant is realized, and a new component material with excellent performance is expected to be obtained. Therefore, the inventor finds that M ions (titanium Ti, chromium Cr, manganese Mn, cobalt Co) are the second luminescence centers occupying silicon lattice sites and have the same Si with the M ions through a large number of experiments and researches⁴⁺The ionic radii are similar; and impurity energy level is introduced into forbidden band and is lower than Ce³⁺Lowest excited state 5d₁Form Ce³⁺→ M radiationless transition energy transfer; the excited state of M ion is degenerated by radiationless process or has no obvious emission peak in visible light region. When doped on silicon sites, other than Ce is introduced³⁺The second competitive luminescence center except ions obviously shortens the time characteristic, but does not introduce other Ce in the visible region³⁺External emission peak due to Ce³⁺The 4f-5d dipole allows transition, the fluorescence lifetime of the transition is much shorter than that of d-d or f-f transition of dipole forbidden resistance, and the introduction of extra emission inevitably causes a plurality of time components, thus being not beneficial to the application of nuclear radiation detection. The rare earth orthosilicate scintillation material with the silicon lattice doped competitive luminescence center has ultrafast luminescence, and can be better applied to high-energy physical detection, particle discrimination and fast nuclear medicine imaging (TOF-PET, PET-CT and PET-MRI).

Preferably, the RE is at least one selected from La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, Sc, Y, preferably at least one selected from Lu, Y, Gd, La.

Preferably, other doping elements A are added into the rare earth orthosilicate scintillation material with silicon lattice doped competitive luminescence center, and the chemical formula is RE_2(1-x-a)Ce_2xA_2aSi_1-yM_yO₅A is more than 0 and less than or equal to 0.01; the other doping element A is at least one selected from Li, Na, K, Rb, Cs, Mg, Ca, Sr, Sc and CuAnd (4) seed preparation.

Preferably, the rare earth orthosilicate scintillation material with silicon lattice doped competitive luminescence center is rare earth orthosilicate scintillation polycrystalline powder with silicon lattice doped competitive luminescence center, rare earth orthosilicate scintillation ceramic with silicon lattice doped competitive luminescence center, or rare earth orthosilicate scintillation single crystal with silicon lattice doped competitive luminescence center.

In a second aspect, the present invention provides a method for preparing a scintillation polycrystalline powder of rare earth orthosilicate with silicon lattice doped with competitive luminescence centers, which is characterized by comprising:

(1) weighing at least one of oxide and carbonate of A, oxide of M, CeO and/or rare earth orthosilicate scintillation polycrystalline powder with silicon lattice doped with competitive luminescence center₂、SiO₂Mixing with RE oxide to obtain mixed powder;

(2) and carrying out solid phase reaction on the obtained mixed powder at 1000-2000 ℃ for 5-200 hours to obtain cerium co-doped orthosilicate scintillation polycrystalline powder.

In a third aspect, the invention provides a preparation method of a rare earth orthosilicate scintillation ceramic with silicon lattice site doped competitive luminescence center, which is characterized by comprising the following steps:

(1) weighing at least one of oxide A and carbonate A, oxide M and CeO according to the chemical formula of the rare earth orthosilicate scintillation ceramic with silicon lattice doped competitive luminescence center₂、SiO₂Mixing with RE oxide to obtain mixed powder;

(2) pressing the obtained mixed powder, and carrying out solid phase reaction for 5-200 hours at 1000-2000 ℃ to obtain cerium co-doped orthosilicate scintillating ceramic; preferably, the pressure for the press molding is 0.03GPa to 5 GPa.

In a fourth aspect, the invention provides a method for preparing a rare earth orthosilicate scintillation single crystal with silicon lattice site doped competitive luminescence centers, which is characterized by comprising the following steps:

(1) weighing at least one of oxide A and carbonate A, oxide M and CeO according to the chemical formula of the rare earth orthosilicate scintillation ceramic with silicon lattice doped competitive luminescence center₂、SiO₂Mixing with RE oxide to obtain mixed powder;

(2) heating the obtained mixed powder to be molten, and growing the rare earth orthosilicate scintillation single crystal with the silicon lattice doped competition luminescence center by adopting a pulling method, a Bridgman method, a temperature gradient method, a heat exchange method, a kyropoulos method, a top seed crystal method, a fluxing agent crystal growth method or a micro-pulling down method.

In a fifth aspect, the invention provides applications of the rare earth orthosilicate scintillation ceramic with the silicon lattice doped competitive luminescence center and the rare earth orthosilicate scintillation single crystal with the silicon lattice doped competitive luminescence center in the fields of high-energy physical detection and particle discrimination and fast nuclear medical imaging.

Has the advantages that:

1. the patent provides a technical scheme that a luminescent activation center is introduced into a silicon lattice of a rare earth orthosilicate scintillation material and competes with a luminescent center of a rare earth lattice, the two activation centers are separated from each other at different lattices, so that the two activation centers are prevented from being gathered in a non-uniform manner in a matrix, the concentration quenching effect is avoided to a certain extent, the steric hindrance is increased, a small part of slow components of a first activation center are transferred to a second activation center, and the time performance of the first activation center is shortened under the condition of no extra emission introduction;

2. after the silicon lattice site of the rare earth orthosilicate scintillation material is introduced into a competitive luminescence center, the output/yield of scintillation light is improved or the luminescence decay time and rise time of the scintillation light are greatly shortened;

3. ultrafast luminescence obtained by doping silicon lattice sites of rare earth orthosilicate scintillating materials in competitive luminescence centers can be better applied to high-energy physical detection and particle discrimination and fast nuclear medicine imaging (TOF-PET, PET-CT and PET-MRI).

Drawings

FIG. 1 is a scintillation decay time profile and fitting results for a scintillation material prepared in example 5;

FIG. 2 is a plot of scintillation rise time for a scintillation material prepared in example 5;

FIG. 3 is a scintillation decay time profile and fitting results for the non-transparent ceramic prepared in example 12;

FIG. 4 is a graph of scintillation rise time for a non-transparent ceramic prepared in example 12;

FIG. 5 is an emission spectrum (358nm excitation) prepared in example 4;

FIG. 6 is an emission spectrum (358nm excitation) of a non-transparent ceramic prepared in example 9.

Detailed Description

The present invention is further illustrated by the following examples, which are to be understood as merely illustrative and not restrictive.

In the present disclosure, the rare earth sites of the rare earth orthosilicate scintillating material contain Ce³⁺Ions are used as luminescence centers, and a competition relationship is formed between the ions and silicon lattice sites doped with second luminescence centers M (═ Ti, Cr, Mn and Co), so that Ce is remarkably improved³⁺The luminous performance, specifically the scintillation light output/light yield is increased or the decay time and the rise time are shortened, and the chemical formula can be written as follows: RE_2(1-x)Ce_2xSi_(1-y)M_yO₅(where RE is a rare earth ion, 0 < x.ltoreq.0.05 (preferably 0.001. ltoreq. x.ltoreq.0.005), M is a second luminescence center occupying a silicon lattice site, 0 < y.ltoreq.0.1 (preferably 0.001. ltoreq. y.ltoreq.0.015) in excess of M, which results in significant deterioration of any of scintillation light output/light yield, energy resolution, fluorescence emission intensity, or X-ray excitation emission intensity, and difficulty in producing a complete single crystal with too high an impurity content_2(1-x)Ce_2xSi_(1-y)M_yO₅Adding another dopant, specifically including at least one of Li, Na, K, Rb, Cs, Mg, Ca, Sr, Sc, and Cu.

In the invention, the second luminescent center M and Ce are doped in the silicon lattice site of the rare earth orthosilicate scintillation material³⁺The luminescent centers form a competitive relationship to realize Ce³⁺Lowest excited state 5d₁A very small part of the slow component of (1) passes through Ce³⁺The energy of the → M nonradiative transition is transferred to the lower excited state of the impurity M in the forbidden band, and then the slow time component is remarkably reduced through the annealing of the nonradiative process or no obvious emission peak in the visible region, thereby achieving the purpose of shortening the time characteristic. Wherein the luminescence includes scintillation luminescence and photoluminescence.

In the present invention, by doping the second luminescence center in the silicon lattice site of the rare earth orthosilicate scintillator material, the luminescence rise time or decay time of the resulting material is shortened, and at least one of improvement in scintillation light output/light yield, reduction in energy resolution, enhancement in fluorescence emission intensity or X-ray excitation emission intensity, and the like is partially (for example, Ti ion) achieved.

In the present invention, y of 0.015 to 0.1 results in any one of scintillation light output/light yield, energy resolution, fluorescence emission intensity or X-ray excitation emission intensity, and performance degradation of > 20%, while achieving a reduction in light emission rise time or decay time.

The preparation method of the rare earth orthosilicate scintillation material with silicon lattice doped competitive luminescence center provided by the invention is exemplarily described as follows. The obtained rare earth orthosilicate scintillation material with silicon lattice doped competitive luminescence center is polycrystalline powder or ceramic or single crystal. Wherein the ceramic includes transparent ceramic and non-transparent ceramic.

Adopting silicon site competition luminescent doping element oxide (M)_aO_b)、CeO₂、SiO₂Rare earth oxide (RE)_mO_n) As raw materials, and mixing the raw materials according to the molar weight of the raw material components_aO_b:CeO₂:SiO₂:RE_mO_nAnd (2) preparing materials according to the ratio of y/a to 2x (1-y) to 2(1-x)/m, and fully and uniformly mixing to obtain mixed powder. a, b, m, n are the number moieties of the chemical formula of the reagents used. The purity of the used raw materials is more than 99.99 percent (4N).

Directly calcining the mixed powder at the temperature of 1000-2000 ℃ for 5-200h to perform solid phase reaction to obtain the polycrystalline powder. Wherein, the temperature of the solid phase reaction can be 1300-1600 ℃, and the time can be 10-50 h.

Or pressing the mixed powder into blocks by 0.03-5GPa, and sintering the blocks at the temperature of 1000-2000 ℃ for 5-200h to obtain the ceramic or preparing the transparent ceramic by regulating and controlling the sintering process. For example, the transparent ceramic is prepared by adopting a sintering process of hot-pressing sintering, vacuum sintering and other technical means. Wherein, the temperature of the solid phase reaction can be 1300-1600 ℃, and the time can be 10-50 h. The briquetting pressure is preferably 2-3 GPa.

Or at least one of polycrystalline powder, transparent ceramic grinding powder, mixed powder and the like is put into a container as a raw material to be melted by heating (resistance or electromagnetic induction or light and the like), and the raw material is slowly crystallized from the melt to prepare a single crystal, wherein the specific method comprises a pulling method, a crucible descending method, a temperature gradient method, a heat exchange method, a kyropoulos method, a top seed crystal method, a fluxing agent crystal growth method and a micro-pulling-down method (mu-PD) for growth.

In the single crystal preparation process, the container can be a graphite crucible, an iridium crucible, a molybdenum crucible, a tungsten-molybdenum crucible, a rhenium crucible, a tantalum crucible, an alumina crucible or a zirconia crucible. The atmosphere for single crystal growth can be one or more of air, argon, nitrogen, carbon dioxide and carbon monoxide. Preferably, the crystal is grown by a pulling method, a container is an iridium crucible, induction heating is adopted, high-purity nitrogen is adopted in the growing atmosphere, pulling is carried out while rotating, the pulling speed is 0.7-6.0 mm/h, and the rotating speed is 3-20 r/min.

The ceramic and single crystal obtained above were pulverized and ground into powder.

In the invention, the rare earth orthosilicate based silicon lattice site is doped with the second luminescent center and Ce³⁺The mutual competition of the luminescence centers obviously improves the Ce³⁺A method for preparing a material with excellent luminous performance.

In the invention, ultrafast luminescence obtained by doping silicon lattice sites of the rare earth orthosilicate scintillating material in the competitive luminescence center can be better applied to high-energy physical detection, particle discrimination and fast nuclear medicine imaging (TOF-PET, PET-CT and PET-MRI).

The present invention will be described in detail by way of examples. It is also to be understood that the following examples are illustrative of the present invention and are not to be construed as limiting the scope of the invention, and that certain insubstantial modifications and adaptations of the invention by those skilled in the art may be made in light of the above teachings. The specific process parameters and the like of the following examples are also only one example of suitable ranges, i.e., those skilled in the art can select the appropriate ranges through the description herein, and are not limited to the specific values exemplified below.

Example 1 (growing Lu)_1.798Y_0.2Ce_0.002Si_(1-y)Ti_yO₅Single crystal)

A Czochralski method is adopted to grow single crystals. TiO is proportioned according to molar weight₂:CeO₂:SiO₂:Lu₂O₃:Y₂O₃0.002 (1-y) and 0.899:0.1 (wherein y is 0.001, 0.003, 0.005, 0.01 and 0.015), fully mixing, pressing the mixture into blocks under 2500MPa cold isostatic pressure, putting the blocks into an iridium crucible, heating and fully melting by induction, inoculating seed crystals, and slowly pulling and growing single crystals with preset size from the melt to obtain Lu_1.798Y_0.2Ce_0.002Si_(1-y)Ti_yO₅And (3) single crystal. Wherein, parameters of the pulling method comprise: the required size parameter design, PID quality control temperature, pulling speed of 3-6 mm/h and rotating speed of 3-5 r/min.

Example 2 (preparation of Lu)_1.798Y_0.2Ce_0.002Si_(1-y)Ti_yO₅Polycrystalline powder body

The materials are mixed according to the example 1, the mixture is fully and evenly mixed, the powder mixture is put into a corundum crucible and put into a muffle furnace to be calcined for 10 hours at 1600 ℃ for solid phase reaction, and Lu is obtained_1.798Y_0.2Ce_0.002Si_(1-y)Ti_yO₅A polycrystalline powder.

Example 3 (preparation of Lu)_1.798Y_0.2Ce_0.002Si_(1-y)Ti_yO₅Ceramic)

Non-transparent state: the materials are mixed according to the example 1, the mixture is fully and evenly mixed, the mixture is pressed into blocks under 30MPa cold isostatic pressure, the blocks are put into a corundum crucible and put into a muffle furnace to be sintered for 10 hours at 1600 ℃ for solid phase reaction, and Lu is obtained_1.798Y_0.2Ce_0.002Si_(1-y)Ti_yO₅A non-transparent ceramic. Transparent: proportioning according to example 1, fully mixing uniformly, pressing the mixture into blocks under cold isostatic pressure of 5000MPa, carrying out solid phase reaction in a vacuum hot pressing furnace, removing bubbles and gaps as much as possible to obtain Lu_1.798Y_0.2Ce_0.002Si_(1-y)Ti_yO₅A transparent ceramic.

Example 4 (growing Lu)_1.798Y_0.2Ce_0.002Si_(1-y)Cr_yO₅Doped single crystal)

Proportioning Cr according to molar weight₂O₃:CeO₂:SiO₂:Lu₂O₃:Y₂O₃Y/2:0.002 (1-y):0.899:0.1 compounding (y ═ 0.0005 and 0.002), the subsequent steps are the same as in example 1, Lu is obtained_1.798Y_0.2Ce_0.002Si_(1-y)Cr_yO₅And (3) single crystal.

Example 5 (preparation of Lu)_1.798Y_0.2Ce_0.002Si_(1-y)Cr_yO₅Polycrystalline powder body

Lu was obtained by blending the ingredients of example 4 and the subsequent steps of example 2_1.798Y_0.2Ce_0.002Si_(1-y)Cr_yO₅A polycrystalline powder.

Example 6 (preparation Lu)_1.798Y_0.2Ce_0.002Si_(1-y)Cr_yO₅Ceramic)

Lu was obtained by blending the ingredients of example 4 and the subsequent steps of example 3_1.798Y_0.2Ce_0.002Si_(1-y)Cr_yO₅Non-transparent ceramics and transparent ceramics.

Example 7 (growing Lu)_1.798Y_0.2Ce_0.002Si_(1-y)Mn_yO₅Single crystal)

MnO in molar ratio₂:CeO₂:SiO₂:Lu₂O₃:Y₂O₃0.002 (1-y) 0.899:0.1 (y is 0.001, 0.003, 0.005, 0.01, 0.03, 0.05, 0.1) and the subsequent steps are the same as in example 1 to obtain Lu_1.798Y_0.2Ce_0.002Si_(1-y)Mn_yO₅And (3) single crystal.

Example 8 (preparation of Lu)_1.798Y_0.2Ce_0.002Si_(1-y)Mn_yO₅Polycrystalline powder body

Lu was obtained by blending the ingredients of example 7 and performing the subsequent steps in the same manner as in example 2_1.798Y_0.2Ce_0.002Si_(1-y)Mn_yO₅A polycrystalline powder.

Example 9 (preparation of Lu)_1.798Y_0.2Ce_0.002Si_(1-y)Mn_yO₅Ceramic)

Lu was obtained by blending the ingredients of example 7 and performing the subsequent steps in the same manner as in example 3_1.798Y_0.2Ce_0.002Si_(1-y)Mn_yO₅Non-transparent ceramics and transparent ceramics.

Example 10 (growing Lu)_1.798Y_0.2Ce_0.002Si_(1-y)Co_yO₅Single crystal)

Proportioning Co according to molar weight₂O₃:CeO₂:SiO₂:Lu₂O₃:Y₂O₃Y/2:0.002 (1-y):0.899:0.1 compounding (y ═ 0.001 and 0.003), the subsequent steps are the same as in example 1 to obtain Lu_1.798Y_0.2Ce_0.002Si_(1-y)Co_yO₅And (3) single crystal.

Example 11 (preparation of Lu)_1.798Y_0.2Ce_0.002Si_(1-y)Co_yO₅Polycrystalline powder body

Proportioning Co according to molar weight₂O₃:CeO₂:SiO₂:Lu₂O₃:Y₂O₃Y/2:0.002 (1-y) 0.899:0.1 compounding (y 0.001, 0.003, 0.005, 0.01, 0.03, 0.05, 0.1), the subsequent steps are the same as in example 2 to obtain Lu_1.798Y_0.2Ce_0.002Si_(1-y)Co_yO₅A polycrystalline powder.

Example 12 (preparation of Lu)_1.798Y_0.2Ce_0.002Si_(1-y)Co_yO₅Ceramic)

Lu was obtained by blending the ingredients of example 10 and performing the subsequent steps in the same manner as in example 3_1.798Y_0.2Ce_0.002Si_(1-y)Co_yO₅Non-transparent ceramics and transparent ceramics.

Example 13 (growing Lu)_1.798-2xY_0.2Ce_2xSi_(1-y)Ti_yO₅Single crystal)

A Czochralski method is adopted to grow single crystals. TiO is proportioned according to molar weight₂:CeO₂:SiO₂:Lu₂O₃:Y₂O₃0.899-x:0.1 (x is 0.001, 0.003, 0.005; y is 0.001, 0.003, 0.005, 0.015), mixing, pressing the mixture into blocks under 2500MPa cold isostatic pressure, placing the blocks into an iridium crucible, heating by induction and melting completely, inoculating seed crystals, and slowly pulling out single crystals with preset size from the melt to obtain Lu_1.798-2xY_0.2Ce_2xSi_(1-y)Ti_yO₅And (3) single crystal. Wherein, parameters of the pulling method comprise: the required size parameter design, PID quality control temperature, pulling speed of 2-6 mm/h and rotating speed of 10-20 r/min.

Example 14 (growing Lu)_2(1-x)Ce_2xSi_(1-y)Cr_yO₅Single crystal)

A Czochralski method is adopted to grow single crystals. Proportioning Cr according to molar weight₂O₃:CeO₂:SiO₂:Lu₂O₃2x (1-y) and (1-x) preparing (x is 0.001, 0.003, 0.005, 0.01, 0.03 and 0.05; y is 0.001, 0.003, 0.005, 0.01, 0.03, 0.05 and 0.1), fully mixing uniformly, pressing the mixture into blocks under 2500MPa cold isostatic pressure, placing the blocks into an iridium crucible, heating and fully melting by induction, slowly pulling and growing single crystals with preset sizes from the melt after seed crystal inoculation to obtain Lu_2(1-x)Ce_2xSi_(1-y)Cr_yO₅And (3) single crystal. Wherein, parameters of the pulling method comprise: the required size parameter design, PID quality control temperature, pulling speed of 0.7-2 mm/h and rotating speed of 3-5 r/min.

Example 15 (Green)Long Y_1.998Ce_0.002Si_(1-y)Cr_yO₅Single crystal)

Proportioning Cr according to molar weight₂O₃:CeO₂:SiO₂:Y₂O₃Y/2:0.002 (1-Y) 0.999 ingredient (Y is 0.001, 0.003, 0.005, 0.01, 0.03, 0.05, 0.1), well mixed, the subsequent steps are the same as example 1 to obtain Y_1.998Ce_0.002Si_(1-y)Cr_yO₅And (3) single crystal.

Example 16 (growing Gd)_2(1-x)Ce_2xSi_(1-y)Co_yO₅Single crystal)

A Czochralski method is adopted to grow single crystals. Proportioning Co according to molar weight₂O₃:CeO₂:SiO₂:Gd₂O₃2x (1-y) preparing (1-x) ingredients (x is 0.001, 0.003, 0.005, 0.01, 0.03 and 0.05; y is 0.001, 0.003, 0.005, 0.01, 0.03, 0.05 and 0.1), fully mixing uniformly, pressing the mixture into blocks under the cold isostatic pressure of 5000MPa, placing the blocks into an iridium crucible, heating and fully melting by induction, slowly pulling and growing a monocrystal with a preset size from the melt after seed crystal inoculation to obtain Gd_2(1-x)Ce_2xSi_(1-y)Co_yO₅And (3) single crystal. Wherein, parameters of the pulling method comprise: the required size parameter design, PID quality control temperature, pulling speed of 1-4 mm/h and rotating speed of 8-20 r/min.

Example 17 (preparation of Gd)_2(1-x)Ce_2xSi_(1-y)Mn_yO₅Ceramic)

Non-transparent state: MnO in molar ratio₂:CeO₂:SiO₂:Gd₂O₃2x (1-y) preparing (1-x) ingredients (x is 0.001, 0.003, 0.005, 0.01, 0.03 and 0.05; y is 0.001, 0.003, 0.005, 0.01, 0.03, 0.05 and 0.1), fully and uniformly mixing, pressing the mixture into blocks under 30MPa cold isostatic pressure, putting the blocks into a corundum crucible, putting the corundum crucible into a muffle furnace, sintering for 5 hours at 2000 ℃ to perform solid phase reaction to obtain Gd_2(1-x)Ce_2xSi_(1-y)Mn_yO₅A non-transparent ceramic. Transparent: mixing the materials according to the molar weight ratio and fully mixingMixing uniformly, pressing the mixture into blocks under cold isostatic pressure of 5000MPa, performing solid phase reaction in a vacuum hot pressing furnace, removing bubbles and gaps as much as possible to obtain Gd_2(1-x)Ce_2xSi_(1-y)Mn_yO₅A transparent ceramic.

Example 18 (growing Gd)_2(1-x-w-z)Lu_2wY_2zCe_2xSi_(1-y)Mn_yO₅Single crystal)

MnO in molar ratio₂:CeO₂:SiO₂:Gd₂O₃:Lu₂O₃:Y₂O₃(1-x-w-z) z ingredient (x: 0.001, 0.003, 0.005, 0.01, 0.03, 0.05, y: 0.001, 0.003, 0.005, 0.01, 0.03, 0.05, 0.1, 0.2, 0.3, 0.4, 0.5, 0.6, 0.7, 0.8, 0.9, z: 0.9, 0.8, 0.7, 0.6, 0.5, 0.4, 0.3, 0.2, 0.1) z, Gd obtained in the same manner as in example 1, followed by Gd obtaining_2(1-x-w-z)Lu_2wY_2zCe_2xSi_(1-y)Mn_yO₅And (3) single crystal.

FIG. 1 is Lu_1.798Y_0.2Ce_0.002Si_(1-y)Cr_yO₅(y is 0, 0.05%, 0.2%) and fitting results, it is known that the decay time after the silicon site doped Cr competition center is shortened from 39ns to 37 and 34 ns.

FIG. 2 is Lu_1.798Y_0.2Ce_0.002Si_(1-y)Cr_yO₅(y is 0, 0.05%, 0.2%) scintillation rise time profile of the polycrystalline powder (the time required for each sample to rise to the maximum value can be seen by fixing the maximum value point of all samples at time zero, and the rise time of 0.05% Cr doping can be seen as the shortest).

FIG. 3 is Lu_1.798Y_0.2Ce_0.002Si_(1-y)Co_yO₅(y is 0, 0.1%, 0.3%) scintillation decay time map of the non-transparent ceramic and fitting results (solid line is decay time fitting curve without Co doping; dotted line is decay time fitting curve with 0.3% Co doping), from which it can be seen that the silicon site doped Co competesThe post-center decay time is shortened from 41ns to 28 ns.

FIG. 4 is Lu_1.798Y_0.2Ce_0.002Si_(1-y)Co_yO₅(y is 0, 0.1%, 0.3%) scintillation rise time map of non-transparent ceramic (the time required for each sample to rise to the maximum can be seen by fixing the maximum point of all samples at time zero, and the rise time of 0.1% Co doping can be seen as the shortest);

FIG. 5 and FIG. 6 are Y_1.998Ce_0.002Si_(1-y)Cr_yO₅(y ═ 0, 0.1%, 0.2%, 0.5%, 2%) single crystal and Lu_1.798Y_0.2Ce_0.002Si_(1-y)Mn_yO₅(y is 0, 0.3%, 2%) the fluorescence spectrum (358nm excitation) of the non-transparent ceramic, and it is understood from the graph that the emission peak is Ce³⁺The 5d-4f transition of (a) has no second emission peak. From its intensity, it can be seen that a content of M ions greater than the preferred value leads to a deterioration of the fluorescence emission intensity by > 20%.

Table 1 summarizes the decay times of some of the silicon lattice doped competitive luminescence center rare earth orthosilicate scintillating materials.

The above examples are only for further illustration of the present invention and should not be construed as limiting the scope of the present invention, and the non-essential modifications and adaptations of the present invention by those skilled in the art based on the foregoing descriptions are within the scope of the present invention.