Preparation method and application of start-up glass for electric melting furnace for glass solidification of high-level radioactive waste in power pile

Abstract

The present invention relates to the technical field of high-level radioactive liquid waste treatment, and proposes a method for preparing and applying starter glass for a power reactor high-level radioactive liquid waste vitrification electric melting furnace. The preparation method comprises the following steps: S1, uniformly mixing starter glass raw materials containing SiO2, B2O3, Na2O, Li2O, Al2O3, CaO, ZnO, BaO, ZrO2, La2O3, CeO2, Nd2O3, and Fe2O3, and melting them at high temperature to produce a glass melt; S2, quenching the glass melt obtained in step S1 to obtain the starter glass. The ZnO in the starter glass of the present invention exists primarily as [ZnO4] tetrahedrons in the glass, stabilizing the glass network, inhibiting the precipitation of silicate crystals, and ensuring the thermal and chemical stability of the glass.

Description

Technical Field

[0001] The present invention relates to the technical field of high-level radioactive liquid waste treatment, and in particular to a preparation method and application of start-up glass for a power pile high-level radioactive liquid waste glass solidification electric melting furnace. Background Art

[0002] Joule-heated ceramic electric melting furnaces are currently the most widely used process for vitrification of high-level radioactive liquid waste due to their simple process flow, high melting efficiency, and long furnace life. Their principle utilizes the electrical conductivity of high-temperature molten glass. Current passing through electrodes immersed in the glass generates Joule heat within the glass bath, thereby melting the top layer of material. Therefore, to start the furnace, a certain amount of starter glass must be added. The starter glass is then melted within the furnace using an external heat source, such as silicon-carbon rods or silicon-molybdenum rods. Once the starter glass is melted, the electrodes are energized, completing the process.

[0003] The composition of the starter glass is a key factor influencing the success of the startup. To ensure stable operation of a Joule ceramic heating electric furnace, the properties of the starter glass must match those of the final waste vitreous solid. Therefore, the starter glass must be easy to prepare and maintain process properties such as melt conductivity and viscosity similar to those of the final waste vitreous solid. This prevents sudden changes in melt conductivity and viscosity after the addition of high-level radioactive waste and glass matrix batch materials, which could lead to furnace accidents.

[0004] More critically, under radiation conditions, it is extremely difficult to replace external heat source components. Therefore, once an electric furnace is started, it is usually not shut down. Even if external facilities need to be repaired, only the feeding will be stopped, and start-up glass will be added to replace the radioactive waste glass. The electrodes will be kept energized and the furnace will be idle to keep warm. The idling and insulation time can be as short as a few days or as long as several months. During the idling and insulation process, the temperature of the glass melting pool in the furnace is usually maintained at 800-1000℃. At this time, the top of the glass melting pool is no longer covered by a cold cap layer, and elements such as Na and B are extremely volatile, affecting the chemical composition of the glass melt, which may cause the precipitation of silicate mineral crystals during the long-term idling and insulation process, blocking the furnace discharge port and affecting the normal operation of the furnace. Summary of the Invention

[0005] In view of this, the present invention proposes a preparation method and application of starting glass for a powered high-level radioactive waste glass solidification electric melting furnace, so as to solve the problem that the existing glass solidification process is prone to crystallization of starting glass during long-term idling and insulation, which blocks the furnace discharge port and affects the normal operation of the furnace.

[0006] The technical solution of the present invention is achieved as follows: On the one hand, the present invention provides a method for preparing starting glass for a power pile high-level radioactive waste liquid glass solidification electric melting furnace, comprising the following steps:

[0007] S1, mixing starting glass raw materials containing SiO2, B2O3, Na2O, Li2O, Al2O3, CaO, ZnO, BaO, ZrO2, La2O3, CeO2, Nd2O3 and Fe2O3 uniformly, and melting them at a high temperature to obtain a glass melt;

[0008] S2, quenching the glass melt obtained in step S1 to obtain starting glass.

[0009] In the starting glass of the present invention, SiO2 and B2O3 are glass network formers and are the basic components of the glass; Al2O3 is a glass network intermediate and can act as a tetracoordinate (Al IV ) network formers, and can also act as pentacoordinate (Al V ) or six-coordinated (Al VI ) plays a charge compensation role; Li2O, Na2O, CaO and BaO are glass network modifiers, which are used to improve the glass melting process and reduce the glass viscosity; at the same time, in order to maintain a similar chemical composition and properties between the starting glass and the final waste glass solid body, some major components of high-level radioactive waste are also introduced into the starting glass: ZrO2, La2O3, CeO2, Nd2O3 and Fe2O3.

[0010] Borosilicate glass is prone to phase separation during heat treatment, forming localized high-Al regions that provide precursor structures and nucleation sites for the precipitation of calcium-aluminosilicate minerals. ZnO, primarily present in glass as [ZnO4] tetrahedrons, has a similar structural role to Al2O3, replacing and dispersing Al, thereby inhibiting the precipitation of calcium-aluminosilicate minerals and ensuring the thermal and chemical stability of the glass.

[0011] On the basis of the above technical solution, preferably, the starting glass raw materials include the following components, calculated by mass percentage of oxides: SiO2: 40~50wt%, B2O3: 8~18wt%, Na2O: 5~12wt%, Li2O: 1~3wt%, Al2O3: 2~7wt%, CaO: 2~8wt%, ZnO: 1~4wt%, BaO: 0~2wt%, ZrO2: 1~4wt%, La2O3: 1~5wt%, CeO2: 1~4wt%, Nd2O3: 1~4wt%, Fe2O3: 1~2 wt%.

[0012] On the basis of the above technical solution, preferably, the starting glass further includes GeO2.

[0013] GeO2 has a strong network-forming ability and can covalently bond with Si, strengthening the glass's network structure. This reduces the formation of Al-rich regions in the glass, increases the migration barrier for crystallizing elements, and reduces the likelihood of calcium-aluminosilicate crystal precipitation. Therefore, to ensure the thermal and chemical stability of the starting glass, ZnO and GeO2 are introduced into the starting glass. On the one hand, ZnO acts as a network modifier, reducing unstable regions; on the other hand, GeO2 synergistically strengthens the glass's main framework, inhibiting Al enrichment and phase separation. Together, these two factors reduce the risk of calcium-aluminosilicate mineral precipitation, improve the glass's thermal and chemical stability, and ensure the starting glass achieves excellent performance.

[0014] On the basis of the above technical solution, preferably, in the starting glass, the mass percentage of GeO2 oxide is 0.2-1 wt%.

[0015] On the basis of the above technical solution, preferably, the starting glass raw materials include the following components, calculated by mass percentage of oxides: SiO2: 42~50wt%, B2O3: 10~16wt%, Na2O: 8~12wt%, Li2O: 1.5~3wt%, Al2O3: 2~5wt%, CaO: 3~6wt%, ZnO: 1~4wt%, BaO: 0~2wt%, ZrO2: 1~4wt%, La2O3: 2~5wt%, CeO2: 1~4wt%, Nd2O3: 1~4wt%, Fe2O3: 1~2 wt%, GeO2: 0.4~1wt%.

[0016] On the basis of the above technical solution, preferably, in step S1, the temperature of the high-temperature melting is 1100-1300° C., and the time is 1-24 hours.

[0017] On the basis of the above technical solution, preferably, in step S2, the quenching method is water quenching or rapid cooling in air.

[0018] On the basis of the above technical scheme, preferably, SiO2, GeO2, ZnO, ZrO2, La2O3, CeO2, Nd2O3 and Fe2O3 are introduced in the form of oxides, B2O3 is introduced in the form of oxide or H3BO3, Al2O3 is introduced in the form of oxide or Al(OH)3, and Na2O, Li2O, CaO and BaO are introduced in the form of carbonates.

[0019] In a second aspect, the present invention provides a starting glass for a power stack high-level radioactive waste liquid glass solidification electric melting furnace, which is produced by the above-mentioned preparation method.

[0020] In a third aspect, the present invention provides the use of the above-mentioned starting glass in treating high-level radioactive waste from power reactors.

[0021] The preparation method and application of the starting glass for the electric melting furnace for glass solidification of high-level radioactive waste in a power pile of the present invention have the following beneficial effects compared with the prior art.

[0022] (1) The appropriate amount of ZnO in the starting glass of the present invention promotes the stability of the glass network, inhibits the precipitation of calcium aluminum silicate minerals, and ensures the thermal and chemical stability of the glass.

[0023] (2) The appropriate amount of GeO2 in the starting glass of the present invention can covalently bond with Si, strengthen the network structure of the glass, reduce the formation of Al-rich regions in the glass, increase the migration barrier of crystallization elements, and reduce the possibility of precipitation of calcium aluminum silicate. The introduction of ZnO and GeO2 into the starting glass, on the one hand, ZnO acts as a network modifier to reduce the unstable region; on the other hand, GeO2 synergistically strengthens the main skeleton of the glass and inhibits Al enrichment and phase separation. Together, these two factors reduce the risk of crystallization of calcium aluminum silicate, improve the thermochemical stability of the glass, and ensure that the starting glass achieves excellent performance. BRIEF DESCRIPTION OF THE DRAWINGS

[0024] In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the following briefly introduces the drawings required for use in the embodiments or the description of the prior art. Obviously, the drawings described below are only some embodiments of the present invention. For ordinary technicians in this field, other drawings can be obtained based on these drawings without paying any creative work.

[0025] Figure 1 The XRD patterns of the starting glass samples prepared in Examples and Comparative Examples after heat treatment at 800°C for 30 days. DETAILED DESCRIPTION

[0026] The following will be combined with the embodiments of the present invention to clearly and completely describe the technical solutions in the embodiments of the present invention. Obviously, the embodiments described are only part of the embodiments of the present invention, not all of the embodiments. Based on the embodiments of the present invention, all other embodiments obtained by ordinary technicians in this field without making creative efforts are within the scope of protection of the present invention.

[0027] Example 1

[0028] This embodiment provides a starting glass for a power pile high-level radioactive waste liquid glass solidification electric melting furnace and a preparation method thereof.

[0029] The starting glass includes the following components in terms of oxide mass percentage: SiO2: 46wt%, B2O3: 15wt%, Na2O: 10wt%, Li2O: 3wt%, Al2O3: 5wt%, CaO: 2wt%, ZnO: 1wt%, BaO: 2wt%, ZrO2: 4wt%, La2O3: 4wt%, CeO2: 3wt%, Nd2O3: 3wt%, Fe2O3: 2wt%.

[0030] The preparation method is as follows: 100g of starting glass batch is prepared according to the above proportions, wherein SiO2, B2O3, Al2O3, ZnO, ZrO2, La2O3, CeO2, Nd2O3, and Fe2O3 are introduced as oxides, and Na2O, Li2O, CaO, and BaO are introduced as carbonates (Na2CO3, Li2CO3, CaCO3, and BaCO3). After the raw materials are uniformly mixed, they are placed in a crucible and transferred to a muffle furnace for melting at 1150°C for 2 hours. After melting, the crucible is removed and the glass melt is quenched in air to obtain the starting glass.

[0031] Example 2

[0032] Compared with Example 1, Example 2 differs in that the starting glass includes the following components, calculated by mass percentage of oxides: SiO2: 43wt%, B2O3: 15wt%, Na2O: 10wt%, Li2O: 3wt%, Al2O3: 5wt%, CaO: 2wt%, ZnO: 4wt%, BaO: 2wt%, ZrO2: 4wt%, La2O3: 4wt%, CeO2: 3wt%, Nd2O3: 3wt%, Fe2O3: 2wt%.

[0033] In the starting glass, the mass percentage of ZnO oxide is 4 wt %, the mass percentage of SiO 2 oxide is 43 wt %, and the rest of the contents are the same as in Example 1.

[0034] Example 3

[0035] The difference between Example 3 and Example 2 is that the starting glass includes the following components, calculated in terms of oxide mass percentage: SiO2: 42.8wt%, B2O3: 15wt%, Na2O: 10wt%, Li2O: 3wt%, Al2O3: 5wt%, CaO: 2wt%, ZnO: 4wt%, GeO2: 0.2wt%, BaO: 2wt%, ZrO2: 4wt%, La2O3: 4wt%, CeO2: 3wt%, Nd2O3: 3wt%, Fe2O3: 2wt%.

[0036] On the basis of Example 2, 0.2 wt% (mass percentage of oxide) of GeO2 is added. GeO2 is introduced in the form of oxide. The mass percentage of SiO2 oxide is 42.8 wt%. The rest of the contents are the same as in Example 2.

[0037] Example 4

[0038] The difference between Example 4 and Example 2 is that the starting glass includes the following components, calculated in terms of oxide mass percentage: SiO2: 42wt%, B2O3: 15wt%, Na2O: 10wt%, Li2O: 3wt%, Al2O3: 5wt%, CaO: 2wt%, ZnO: 4wt%, GeO2: 1wt%, BaO: 2wt%, ZrO2: 4wt%, La2O3: 4wt%, CeO2: 3wt%, Nd2O3: 3wt%, Fe2O3: 2wt%.

[0039] On the basis of Example 2, 1 wt% (mass percentage of oxide) of GeO2 is added, the mass percentage of SiO2 oxide is 42 wt%, and the rest of the contents are the same as Example 2.

[0040] Example 5

[0041] This embodiment provides a starting glass for a power pile high-level radioactive waste glass solidification electric melting furnace and a preparation method thereof. The preparation method is the same as that of Example 2, except that the components of the starting glass are:

[0042] The starting glass includes the following components in terms of oxide mass percentage: SiO2: 40wt%, B2O3: 16wt%, Na2O: 5wt%, Li2O: 1wt%, Al2O3: 7wt%, CaO: 8wt%, ZnO: 1.6wt%, GeO2: 0.4wt%, BaO: 2wt%, ZrO2: 4wt%, La2O3: 5wt%, CeO2: 4wt%, Nd2O3: 4wt%, Fe2O3: 2wt%.

[0043] Example 6

[0044] This embodiment provides a starting glass for a power pile high-level radioactive waste glass solidification electric melting furnace and a preparation method thereof. The preparation method is the same as that of Example 2, except that the components of the starting glass are:

[0045] The starting glass includes the following components in terms of oxide mass percentage: SiO2: 49wt%, B2O3: 18wt%, Na2O: 12wt%, Li2O: 1.5wt%, Al2O3: 2wt%, CaO: 6wt%, ZnO: 3.2wt%, GeO2: 0.8wt%, ZrO2: 1wt%, La2O3: 2wt%, CeO2: 1wt%, Nd2O3: 2wt%, Fe2O3: 1.5wt%.

[0046] Example 7

[0047] This embodiment provides a starting glass for a power pile high-level radioactive waste glass solidification electric melting furnace and a preparation method thereof. The preparation method is the same as that of Example 2, except that the components of the starting glass are:

[0048] The starting glass includes the following components in terms of oxide mass percentage: SiO2: 50wt%, B2O3: 10wt%, Na2O: 8wt%, Li2O: 3wt%, Al2O3: 4.3wt%, CaO: 3wt%, ZnO: 4wt%, GeO2: 0.2wt%, BaO: 1.5wt%, ZrO2: 2wt%, La2O3: 5wt%, CeO2: 4wt%, Nd2O3: 4wt%, Fe2O3: 1wt%.

[0049] Example 8

[0050] The starting glass includes the following components in terms of oxide mass percentage: SiO2: 50wt%, B2O3: 8wt%, Na2O: 12wt%, Li2O: 3wt%, Al2O3: 3wt%, CaO: 8wt%, ZnO: 4wt%, GeO2: 1wt%, BaO: 2wt%, ZrO2: 3wt%, La2O3: 1wt%, CeO2: 2wt%, Nd2O3: 1wt%, Fe2O3: 2wt%.

[0051] Comparative Example 1

[0052] Compared with Example 1, Comparative Example 1 differs in that the starting glass includes the following components, calculated by mass percentage of oxides: SiO2: 47wt%, B2O3: 15wt%, Na2O: 10wt%, Li2O: 3wt%, Al2O3: 5wt%, CaO: 2wt%, BaO: 2wt%, ZrO2: 4wt%, La2O3: 4wt%, CeO2: 3wt%, Nd2O3: 3wt%, Fe2O3: 2wt%.

[0053] Comparative Example 1 lacks ZnO, the mass percentage of SiO2 oxide is 47wt%, and the rest of the contents are the same.

[0054] Comparative Example 2

[0055] Compared with Example 3, Comparative Example 2 differs in that the starting glass includes the following components, calculated by mass percentage of oxides: SiO2: 43wt%, B2O3: 15wt%, Na2O: 10wt%, Li2O: 3wt%, Al2O3: 5wt%, CaO: 2wt%, ZnO: 4wt%, BaO: 2wt%, ZrO2: 4wt%, La2O3: 4wt%, CeO2: 3wt%, Nd2O3: 3wt%, Fe2O3: 2wt%.

[0056] Comparative Example 2 lacks GeO2 and only adds ZnO. The mass percentage of SiO2 oxide is 43wt%, and the rest of the contents are the same.

[0057] Comparative Example 3

[0058] Compared with Example 1, Comparative Example 3 differs in that the starting glass includes the following components, calculated by mass percentage of oxides: SiO2: 40wt%, B2O3: 15wt%, Na2O: 10wt%, Li2O: 3wt%, Al2O3: 5wt%, CaO: 2wt%, ZnO: 7wt%, BaO: 2wt%, ZrO2: 4wt%, La2O3: 4wt%, CeO2: 3wt%, Nd2O3: 3wt%, Fe2O3: 2wt%.

[0059] The content of ZnO exceeds the limit, specifically 7 wt% (mass percentage of oxide), the mass percentage of SiO2 oxide is 40 wt%, and the rest of the contents are the same.

[0060] Comparative Example 4

[0061] Compared with Example 3, Comparative Example 4 differs in that the starting glass includes the following components, calculated by mass percentage of oxides: SiO2: 38wt%, B2O3: 15wt%, Na2O: 10wt%, Li2O: 3wt%, Al2O3: 5wt%, CaO: 2wt%, ZnO: 4wt%, GeO2: 5wt%, BaO: 2wt%, ZrO2: 4wt%, La2O3: 4wt%, CeO2: 3wt%, Nd2O3: 3wt%, Fe2O3: 2wt%.

[0062] The GeO2 content of Comparative Example 4 exceeds the specified range, specifically 5 wt% (mass percentage of oxide), the mass percentage of SiO2 oxide is 38 wt%, and the rest of the contents are the same.

[0063] Comparative Example 5

[0064] Compared with Comparative Example 1, Comparative Example 5 differs in that the starting glass includes the following components, calculated by mass percentage of oxides: SiO2: 42wt%, B2O3: 15wt%, Na2O: 10wt%, Li2O: 3wt%, Al2O3: 10wt%, CaO: 2wt%, BaO: 2wt%, ZrO2: 4wt%, La2O3: 4wt%, CeO2: 3wt%, Nd2O3: 3wt%, Fe2O3: 2wt%.

[0065] The Al2O3 content of Comparative Example 5 exceeds the specified range, specifically 10 wt% (mass percentage of oxide), the mass percentage of SiO2 oxide is 42 wt%, and the rest of the contents are the same.

[0066] Comparative Example 6

[0067] Comparative Example 6 is different from Comparative Example 1 in that the starting glass comprises the following components, calculated by mass percentage of oxides: SiO2: 39wt%, B2O3: 15wt%, Na2O: 10wt%, Li2O: 3wt%, Al2O3: 5wt%, CaO: 10wt%, BaO: 2wt%, ZrO2: 4wt%, La2O3: 4wt%, CeO2: 3wt%, Nd2O3: 3wt%, Fe2O3: 2wt%

[0068] The CaO content of Comparative Example 6 exceeds the specified range, specifically 10 wt% (mass percentage of oxide), the mass percentage of SiO2 oxide is 39 wt%, and the rest of the contents are the same.

[0069] Comparative Example 7

[0070] Compared with Comparative Example 1, Comparative Example 7 differs in that the starting glass includes the following components, calculated by mass percentage of oxides: SiO2: 43wt%, B2O3: 15wt%, Na2O: 14wt%, Li2O: 3wt%, Al2O3: 5wt%, CaO: 2wt%, BaO: 2wt%, ZrO2: 4wt%, La2O3: 4wt%, CeO2: 3wt%, Nd2O3: 3wt%, Fe2O3: 2wt%.

[0071] The content of Na2O exceeds the limit, specifically 14wt% (mass percentage of oxide), the mass percentage of SiO2 oxide is 43wt%, and the rest of the contents are the same.

[0072] The performance of the starting glass prepared in the above examples and comparative examples was tested by processing the glass into a glass with a surface area of ​​400 mm 2After the surface of the block was polished, a static leaching test was conducted in 40 mL of deionized water. After leaching at 90 ° C for 28 days, the unit surface area mass loss (g / m 2 ).

[0073] Another 40 g starting glass sample was ground into powder, and heat treated at 800° C. for 30 days. The crystallization rate of the starting glass sample was determined by X-ray diffraction analysis.

[0074] The test results are shown in Table 1.

[0075]

[0076] As shown in Table 1, the addition of ZnO and GeO2 to the starting glass not only reduces the crystallization rate, but also enhances the chemical stability of the glass, which is manifested in a significant reduction in the mass loss per unit surface area and the crystallization rate. The lack of ZnO or GeO2 will reduce the performance of the starting glass (see Comparative Examples 1-2). The XRD pattern of the sample after heat treatment shows obvious diffraction peaks of calcium aluminum silicate crystals (see Figure 1 As the amount of ZnO and GeO2 gradually increased, the mass loss per unit surface area and the crystallization rate both showed a downward trend (see Examples 2-4). In the XRD pattern of the heat-treated sample, the intensity of the diffraction peak of the calcium aluminum silicate crystal gradually decreased and disappeared.

[0077] In Comparative Examples 3-4, when the amount of ZnO or GeO2 exceeds the specified range, the mass loss per unit surface area or the crystallization rate shows an increasing trend. This is because the structural balance of the glass is destroyed when ZnO and GeO2 are excessive, which not only affects the thermal and chemical stability of the glass, but also brings application safety risks.

[0078] In Comparative Example 3, excessive ZnO leads to a loose glass network and reduced uniformity, resulting in an increased crystallization rate and reduced chemical stability. GeO2, however, acts as a network former. Adding a small amount of GeO2 to silicate glass can adjust the network, reduce aluminum clusters, and increase the crystallization activation energy of aluminosilicate crystals by competing with SiO2. However, the Ge-O bond energy (~444 kJ / mol) is slightly lower than that of Si-O (~452 kJ / mol). Excessive GeO2 replacing SiO2 in the glass loosens the network structure and reduces the chemical stability of the glass (Comparative Example 4). The crystallization rate of the glass is simultaneously promoted by the loosening of the network and inhibited by the competition, resulting in no significant change.

[0079] In Comparative Examples 5-7, the Al2O3, CaO, and Na2O contents in the starting glasses exceeded the requirements of the present invention, and ZnO and GeO2 were not added to adjust the glass network structure. Consequently, the glasses exhibited a strong tendency to crystallize and poor chemical stability. This is because excessive Al2O3, CaO, and Na2O easily create energetically unstable Al-rich regions and loosely structured regions within the glass, which are highly susceptible to crystallization (especially calcium aluminosilicate crystallization). This also reduces the overall chemical stability of the glass, leading to poor durability and susceptibility to corrosion.

[0080] The above description is only a preferred embodiment of the present invention and is not intended to limit the present invention. Any modifications, equivalent substitutions, improvements, etc. made within the spirit and principles of the present invention should be included in the scope of protection of the present invention.

Claims

1. A method for preparing start-up glass for a power-pile high-level radioactive waste glass solidification electric melting furnace, characterized by: The following steps are involved: S1, containing SiO2, B2O3, Na2O, Li2O, Al2O3, CaO, ZnO, BaO, ZrO2, La2O3, CeO2, Nd2O 3、 The starting glass raw materials of GeO2 and Fe2O3 components are mixed evenly and melted at a high temperature to obtain a glass melt; S2, quenching the glass melt obtained in step S1 to obtain starting glass; Calculated by oxide mass percentage, the starting glass raw materials include the following components: SiO2: 40~50wt%, B2O3: 8~18wt%, Na2O: 5~12wt%, Li2O: 1~3wt%, Al2O3: 2~7wt%, CaO: 2~8wt%, ZnO: 1~4wt%, BaO: 0~2wt%, ZrO2: 1~4wt%, La2O3: 1~5wt%, CeO2: 1~4wt%, Nd2O3: 1~4wt%, GeO2: 0.2~1wt%, Fe2O3: 1~2wt%.

2. The preparation method according to claim 1, wherein: Calculated by oxide mass percentage, the starting glass raw material includes the following components: SiO2: 42~50wt%, B2O3: 10~16wt%, Na2O: 8~12wt%, Li2O: 1.5~3wt%, Al2O3: 2~5wt%, CaO: 3~6wt%, ZnO: 1~4wt%, BaO: 0~2wt%, ZrO2: 1~4wt%, La2O3: 2~5wt%, CeO2: 1~4wt%, Nd2O3: 1~4wt%, Fe2O3: 1~2 wt%, and GeO2: 0.4~1wt%.

3. The preparation method according to claim 1, wherein: In step S1, the high-temperature melting temperature is 1100-1300° C., and the time is 1-24 hours.

4. The preparation method according to claim 1, wherein: In step S2, the quenching method is water quenching or cooling in air.

5. The preparation method according to claim 1, wherein: SiO2, GeO2, ZnO, ZrO2, La2O3, CeO2, Nd2O3 and Fe2O3 are introduced in the form of oxides, B2O3 is introduced in the form of oxide or H3BO3, Al2O3 is introduced in the form of oxide or Al(OH)3, and Na2O, Li2O, CaO and BaO are introduced in the form of carbonates.

6. A starting glass for a power-stacked high-level radioactive waste glass solidification electric melting furnace, characterized by: The method is prepared according to any one of claims 1 to 5.

7. Use of the starting glass as claimed in claim 6 in treating high-level radioactive liquid waste from power reactors.

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