CN114436637A

CN114436637A - High-dielectric-constant high-power microwave ferrite material and preparation method thereof

Info

Publication number: CN114436637A
Application number: CN202210215666.3A
Authority: CN
Inventors: 谢斌; 杨菲; 王殿杰; 廖杨; 任仕晶
Original assignee: CETC 9 Research Institute
Current assignee: CETC 9 Research Institute
Priority date: 2022-03-07
Filing date: 2022-03-07
Publication date: 2022-05-06
Anticipated expiration: 2042-03-07
Also published as: CN114436637B

Abstract

The invention discloses a high-dielectric constant high-power microwave ferrite material, which belongs to the technical field of microwave and magnetic materials and has the chemical formula of Y_{3‑x‑y‑a‑b‑c‑d‑e‑} _fBi_xLa_yLu_zGd_aNd_bSm_cDy_dCa_e+fSn_eZr_fFe_{5‑δ‑e‑f}O₁₂Wherein x is more than or equal to 0.8 and less than or equal to 1.6, y + z is more than or equal to 0 and less than or equal to 0.2, a is more than or equal to 0 and less than or equal to 0.7, b + c is more than or equal to 0.06, d is more than or equal to 0.005 and less than or equal to 0.05, e + f is more than or equal to 0.25 and less than or equal to 0.55, delta is the iron deficiency, and delta is more than or equal to 0.03 and less than or equal to 0.1; the invention has high dielectric constant (the term refers to the relative dielectric constant epsilon)_r) The high-power garnet type microwave ferrite material has high dielectric constant and high-power characteristics and has excellent electromagnetic performance; relative permittivity epsilon_rDielectric loss tan delta > 20_ε＜2×10^‑4Spin linewidth Δ H_kMore than 5 Oe, the ferromagnetic resonance line width delta H is less than or equal to 40 Oe, 4 pi Ms is more than or equal to 1700G, and the Curie temperature Tc is more than 270 ℃; the high-dielectric constant and high-power garnet type microwave ferrite material can effectively reduce the design size of the isolator of the high-power microwave circulator and meet the miniaturization requirement.

Description

High-dielectric-constant high-power microwave ferrite material and preparation method thereof

Technical Field

The invention relates to the technical field of microwave and magnetic materials, in particular to a high-dielectric-constant high-power microwave ferrite material and a preparation method thereof.

Background

The high-power material mainly solves the problem that the power bearing capacity of a device is lowered under high power caused by the high-power nonlinear effect of common materials. The research of the high dielectric constant microwave ferrite material aims to reduce the design size of devices such as a circulator, an isolator and the like so as to meet the requirement of miniaturization and integration; if the dielectric constant of the microwave ferrite is increased to more than 20%, the size of the related device can be reduced by 20% or more, and if the material applied to the high-power microwave device can be compatible with the high dielectric constant performance required by the small-size design, the miniaturization of the power microwave device is very beneficial.

With the development of the related technologies, the requirement for ferrite materials widely applied to microwave devices such as circulators and isolators is higher and higher, and further, the development of ferrite materials suitable for devices with excellent performance becomes one of the important technical directions in the field.

The peak power capacity of the device is mainly determined by the high power critical field h of the material_cThe higher critical field can effectively avoid the situation that the loss is increased due to the high-power nonlinear effect of the material caused by the working environment of the device. Spin linewidth Δ H of high power critical field and material_kClosely related, h_c∝ΔH_k(ω/ω_m) And Δ H_kIs a mark of high power performance of the material, and the peak power P-_c ²∝ΔH_k ²Therefore, increase Δ H_kIs a precondition for increasing the peak power. Spin linewidth Δ H_kThe method has outstanding contradiction with the ferromagnetic resonance line width delta H, and the product performance is difficult to meet the high power capacity of the deviceThe quantity can meet the requirement of the device on low magnetic loss. Doping of fast relaxing ions in the dodecahedral position of garnet-type ferrites for increasing Δ Η_kHowever, the Δ H is rapidly increased, and substitution of the octahedral site for suppressing Δ H deterioration significantly lowers the curie temperature, which affects the temperature characteristics of the material.

In addition, the dielectric constant epsilon of the current high-power garnet materials also exists_rThe problem of low dielectric constant is that Bi is generally carried out at the twelve-surface position³⁺Element substituted Y³⁺But a large amount of Bi³⁺A significant increase in the dielectric constant also causes an increase in Δ H, deteriorating the insertion loss.

At present, there are few reports of garnet ferrite materials having both high dielectric constant and high power characteristics, and only microwave ferrites with single high power performance or ferrites with single high dielectric constant performance, for example, the high power garnet ferrite disclosed in chinese patent CN106220158A has a spinning linewidth Δ H of 13 Oe_kHowever, Δ H as high as 130 Oe makes it impractical to use; sm disclosed in CN 105347782B³⁺The dielectric constant of the doped yttrium-gadolinium high-power microwave ferrite material is only 14 of the conventional value of garnet ferrite material, and the doped yttrium-gadolinium high-power microwave ferrite material still has slightly high delta H of 40-70 Oe, the Curie temperature Tc of 200-240 ℃, and delta H_kBut are not mentioned; the garnet ferrites with high dielectric constant described in CN112456998A, CN 106242547 a, etc. all contain a dielectric constant of more than 20, but have the disadvantages of lower saturation magnetization 4 π Ms, slightly higher ferromagnetic resonance line width Δ H, Curie temperature only around 200 ℃ or no control of dielectric loss; the high dielectric garnet material described in CN 111285673 a has a curie temperature of 200 ℃ or higher, a saturation magnetization of 1800G or higher, and a ferromagnetic resonance linewidth controlled to be 40 to 50 Oe, but does not show dielectric loss and does not have high power characteristics.

Therefore, it would be desirable to coordinate Δ H and Δ H while compounding high dielectric constant and high power characteristics_kThe performance contradiction of the ferrite is controlled, the deterioration of the dielectric performance and the magnetic performance is well controlled, the high-power microwave ferrite material with high dielectric constant is developed,the microwave circulator isolator is beneficial to miniaturization and integration of a high-power microwave circulator isolator.

Disclosure of Invention

It is an object of the present invention to provide a low-loss, high-curie temperature, high-permittivity and high-power microwave ferrite material, so as to solve the above problems.

In order to achieve the purpose, the technical scheme adopted by the invention is as follows: a high-dielectric constant high-power microwave ferrite material has a chemical formula of Y_{3-x-y-a-b-c-d-e-f}Bi_xLa_yLu_zGd_aNd_bSm_cDy_dCa_e+fSn_eZr_fFe_5-δ-e-fO₁₂Wherein x is more than or equal to 0.8 and less than or equal to 1.6, y + z is more than or equal to 0 and less than or equal to 0.2, a is more than or equal to 0 and less than or equal to 0.7, b + c is more than or equal to 0.06, d is more than or equal to 0.005 and less than or equal to 0.05, e + f is more than or equal to 0.25 and less than or equal to 0.55, delta is the iron deficiency, delta is more than or equal to 0.03 and less than or equal to 0.1

The dielectric constant of common garnet-type high power microwave ferrites is low, typically around 14, and is controlled due to Δ H_kThe sharp increase of Δ H caused by the increase and the substitution with the large radius ions at the octahedral sites lowers the curie temperature, and the dodecahedral substitution with the commonly used Bi element raises the dielectric constant, which easily causes the increase of Δ H and deterioration of dielectric loss. In order to solve the problem of ferrite performance deterioration caused by the two performances, the invention provides a garnet microwave ferrite material with low loss, high Curie temperature, high dielectric constant and high power. The invention uses rare earth ion Gd³⁺、Dy³⁺、Sm³⁺、Nd³⁺Combined substitution for increasing Δ H of material_kMeanwhile, the temperature stability of the material is ensured; proper amount of Bi³⁺The dielectric constant of the material is improved, and the sintering temperature of the material is reduced; passing a certain amount of rare earth ions La³⁺、Lu³⁺The combined substitution can improve the Curie temperature of the material, offset the Curie temperature partially reduced by the substitution of the large-radius nonmagnetic ions at the octahedral position, and improve the temperature characteristic of the material; zr⁴⁺、Sn⁴⁺Ion substitution reduces the material anisotropy constant, thereby reducing magnetic loss; proper iron deficiency to suppress deterioration of dielectric loss of material。

The invention is realized by making the dodecahedron Y in the garnet structure³⁺And octahedron Fe³⁺The substitution and doping are carried out to compound two characteristics of high power performance and high dielectric constant, so that the material has high dielectric constant epsilon_rAnd high spin linewidth Δ H_kThe design size of the device can be reduced, the miniaturization and the light weight of a microwave ferrite high-power device are facilitated, and meanwhile, the ferrite has high Curie temperature T_cAnd low dielectric loss tan delta_εAnd the lower ferromagnetic resonance line width delta H is beneficial to the performance stability of the power device.

The second purpose of the invention is to provide a preparation method of the material, which adopts the technical scheme that the preparation method comprises the following steps:

(1) according to the chemical formula Y_{3-x-y-a-b-c-d-e-f}Bi_xLa_yLu_zGd_aNd_bSm_cDy_dCa_e+fSn_eZr_fFe_5-δ-e-fO₁₂Wherein x is more than or equal to 0.8 and less than or equal to 1.6, Y + z is more than or equal to 0 and less than or equal to 0.2, a is more than or equal to 0 and less than or equal to 0.7, b + c is more than or equal to 0.06, d is more than or equal to 0.005 and less than or equal to 0.05, e is more than or equal to 0.25 and less than or equal to 0.55, delta is the iron deficiency, delta is more than or equal to 0.03 and less than or equal to 0.1, and each raw material is calculated and weighed, wherein the raw material is Y and less than or equal to 1.6₂O₃、Gd₂O₃、Dy₂O₃、Sm₂O₃、Nd₂O₃、La₂O₃、Lu₂O₃、Bi₂O₃、CaCO₃、SnO₂、ZrO₂、Fe₂O₃；

(2) Carrying out first wet ball milling on the raw materials, namely, carrying out first mixing wet ball milling on the raw materials weighed in the step (1);

(3) pre-burning, namely drying the slurry obtained in the step (2), and then pre-burning powder, wherein the pre-burning temperature is 900-1000 ℃, and the heat preservation time is 4-6 hours;

(4) performing wet ball milling for the second time, namely performing wet ball milling for the second time on the pre-sintered powder obtained in the step (3) to obtain slurry of the pre-sintered material;

(5) granulating, namely drying the slurry obtained in the step (4), and then adding an adhesive to uniformly mix for granulation;

(6) molding, namely performing compression molding on the powder particles obtained after granulation in the step (5) to obtain green bodies;

(7) and (4) sintering, namely sintering the green body obtained in the step (6), wherein the sintering temperature is 1050-1100 ℃, and the temperature is kept for more than 20 hours, so as to obtain the ceramic material.

As a preferred technical scheme, the purity of the raw material in the step (1) is analytically pure.

As a preferable technical scheme, the ball milling time in the step (2) is 4-6 hours.

As a preferable technical scheme, the adhesive in the step (5) is polyvinyl alcohol (PVA) water solution, and the concentration of the polyvinyl alcohol (PVA) water solution is 5-15 wt%.

Compared with the prior art, the invention has the advantages that: the garnet type microwave ferrite material with high dielectric constant and high power obtained by adopting the combined substitution of a plurality of rare earth ions has the characteristics of high dielectric constant and high power, has excellent electromagnetic performance, higher saturation magnetization intensity of 4 pi Ms and low dielectric loss of tan delta_εSmall ferromagnetic resonance line width Δ H, wide range of high dielectric constant ε and spin wave line width Δ H_k(ii) a Dielectric constant ε_rDielectric loss tan delta > 20_ε＜2×10^-4Spin linewidth Δ H_kMore than 5 Oe, the ferromagnetic resonance line width delta H is less than or equal to 40 Oe, 4 pi Ms is more than or equal to 1700G, and the Curie temperature Tc is more than 270 ℃; the garnet-type microwave ferrite material with high dielectric constant and high power can effectively reduce the design size of the isolator of the high-power microwave circulator and meet the miniaturization requirement.

Drawings

FIG. 1 is a phase analysis XRD result of the ferrite material of example 1;

FIG. 2 is a phase analysis XRD result diagram of the ferrite material of example 2;

FIG. 3 is a phase analysis XRD result diagram of the ferrite material of example 3;

fig. 4 is a phase analysis XRD result pattern of the ferrite material of example 4.

Detailed Description

The invention will be further explained with reference to the drawings.

Example 1

A low-loss high-Curie temperature high-dielectric constant high-power microwave ferrite material with a chemical formula of Y_{3-x-y-a-b-c-d-e-f}Bi_xLa_yLu_zGd_aNd_bSm_cDy_dCa_e+fSn_eZr_fFe_5-δ-e-fO₁₂Where x is 0.8, y =0.1, z is 0, a, b, c is 0, d =0.005, e =0.3, f =0, δ is 0.1;

the preparation method comprises the following steps:

according to the formula Y_{3-x-y-a-b-c-d-e-f}Bi_xLa_yLu_zGd_aNd_bSm_cDy_dCa_e+fSn_eZr_fFe_5-δ-e-fO₁₂Wherein x is 0.8, Y =0.1, z is 0, a, b, c is 0, d =0.005, e =0.3, f =0, δ is 0.1, calculating and weighing each raw material, the raw material is Y₂O₃、La₂O₃、Dy₂O₃、Bi₂O₃、CaCO₃、SnO₂、Fe₂O₃(ii) a Carrying out first mixing wet ball milling on the weighed raw materials, drying the slurry, presintering the powder, keeping the presintering temperature at 1000 ℃ for 5 hours; carrying out wet ball milling on the pre-sintered powder for the second time, drying the slurry, adding an adhesive, uniformly mixing and granulating; then carrying out compression molding; and sintering the molded green body at the sintering temperature of 1080 ℃ for more than 20h to obtain the high-dielectric-constant high-power microwave ferrite material.

The phase analysis of the prepared material was carried out using an X-ray diffraction analyzer (Panalytical X' Pert Powder, the Netherlands), and the results are shown in FIG. 1.

Example 2

A low-loss high-Curie-temperature high-dielectric-constant high-power microwave ferrite materialHas a chemical formula of Y_{3-x-y-a-b-c-d-e-f}Bi_xLa_yLu_zGd_aNd_bSm_cDy_dCa_e+fSn_eZr_fFe_5-δ-e-fO₁₂Where x is 1.0, y = 0.05, z is 0.05, a is 0, b =0.005, c is 0.005, d =0.03, e = 0.30.3, f =0.1, δ is 0.1;

the preparation method comprises the following steps:

according to the formula Y_{3-x-y-a-b-c-d-e-f}Bi_xLa_yLu_zGd_aNd_bSm_cDy_dCa_e+fSn_eZr_fFe_5-δ-e-fO₁₂Wherein x is 1.0, Y is 0.5, z =0.5, a is 0, b =0.005, c is 0.005, d =0.03, e =0.3, f =0.1, δ is 0.1, calculating and weighing each raw material, the raw material is Y₂O₃、Dy₂O₃、La₂O₃、Bi₂O₃、CaCO₃、SnO₂、ZrO₂、Fe₂O₃(ii) a Carrying out first mixing wet ball milling on the weighed raw materials, drying the slurry, presintering the powder, keeping the presintering temperature at 950 ℃, and keeping the temperature for 5 hours; carrying out wet ball milling on the pre-sintered powder for the second time, drying the slurry, adding an adhesive, uniformly mixing and granulating; then carrying out compression molding; and sintering the formed green body at 1070 ℃ for more than 20h to obtain the high-dielectric-constant and high-power microwave ferrite material.

The phase analysis of the prepared material was carried out using an X-ray diffraction analyzer (Panalytical X' Pert Powder, the Netherlands), and the results are shown in FIG. 2.

Example 3

A low-loss high-Curie temperature high-dielectric constant high-power microwave ferrite material with a chemical formula of Y_{3-x-y-a-b-c-d-e-f}Bi_xLa_yLu_zGd_aNd_bSm_cDy_dCa_e+fSn_eZr_fFe_5-δ-e-fO₁₂Where x = 1.3, y =0.1, z = 0.05, a =0.3, b =0.02, c =0.02, d =0, e =0.1, f =0.35, δ = 0.1;

the preparation method comprises the following steps:

according to the formula Y_{3-x-y-a-b-c-d-e-f}Bi_xLa_yLu_zGd_aNd_bSm_cDy_dCa_e+fSn_eZr_fFe_5-δ-e-fO₁₂Wherein x is 1.3, Y =0.1, z is 0.05, a is 0.3, b =0.02, c is 0.02, d =0, e =0.1, f =0.35, δ is 0.1, calculating and weighing each raw material, the raw material is Y₂O₃、Lu₂O₃、Bi₂O₃、Sm₂O₃、Nd2O₃、CaCO₃、SnO₂、ZrO₂、Fe₂O₃(ii) a Carrying out first mixing wet ball milling on the weighed raw materials, drying the slurry, presintering the powder, keeping the presintering temperature at 920 ℃, and keeping the temperature for 5 hours; carrying out secondary wet ball milling on the pre-sintered powder, drying the slurry, adding an adhesive, uniformly mixing, and granulating; then carrying out compression molding; and sintering the molded green body at 1050 ℃ and keeping the temperature for more than 20h to obtain the high-dielectric-constant high-power microwave ferrite material.

The phase analysis of the prepared material was carried out using an X-ray diffraction analyzer (Panalytical X' Pert Powder, the Netherlands), and the results are shown in FIG. 3.

Example 4

A low-loss high-Curie temperature high-dielectric constant high-power microwave ferrite material with a chemical formula of Y_{3-x-y-a-b-c-d-e-f}Bi_xLa_yLu_zGd_aNd_bSm_cDy_dCa_e+fSn_eZr_fFe_5-δ-e-fO₁₂Wherein x is 1.6, y =0.15, z is 0.05, a is 0.6, b =0.03, c is 0.03, d =0, e =0.1, f =0.45, δ is 0.1;

the preparation method comprises the following steps:

according to the formula Y_{3-x-y-a-b-c-d-e-f}Bi_xLa_yLu_zGd_aNd_bSm_cDy_dCa_e+fSn_eZr_fFe_5-δ-e-fO₁₂Wherein x is 1.6, y =0.15, z0.05, 0.5 a, 0.03 b, 0.03 c, 0.03 d, 0.1 e, 0.45 f, 0.1 δ, and Y is calculated and weighed as raw material₂O₃、Lu₂O₃、Gd₂O₃、Bi₂O₃、Nd2O₃、CaCO₃、SnO₂、ZrO₂、Fe₂O₃. Carrying out first mixing wet ball milling on the weighed raw materials, drying the slurry, presintering the powder, keeping the presintering temperature at 900 ℃, and keeping the temperature for 5 hours; carrying out secondary wet ball milling on the pre-sintered powder, drying the slurry, adding an adhesive, uniformly mixing, and granulating; then carrying out compression molding; and sintering the molded green body at 1040 ℃ and keeping the temperature for more than 20h to obtain the high-dielectric-constant high-power microwave ferrite material.

The phase analysis of the prepared material was carried out using an X-ray diffraction analyzer (Panalytical X' Pert Powder, the Netherlands), and the results are shown in FIG. 4.

For the sake of clarity, the following comparative examples are based on example 1, each of which is compared without one factor and with the performance parameters in the subsequent tables being changed.

Comparative example 1

The present comparative example differs from example 1 in that it has the chemical formula:

Y_{3-x-y-a-b-c-d-e-f}Bi_xLa_yLu_zGd_aNd_bSm_cDy_dCa_e+fSn_eZr_fFe_5-δ-e-fO₁₂where x is 0, y =0.1, z is 0, a, b, c =0, d =0.005, e =0.3, f =0, δ is 0.1, ferrite was prepared according to the process flow of example 1, with the pre-firing temperature being changed to 1200 ℃, and the sintering temperature and holding time being 1400 ℃ and 20 hours or more. The comparison factor shows that: comparative example 1 on the basis of example 1, Bi is eliminated³⁺Substituting and retaining non-magnetic rare earth ions La³⁺Trace substitution and retention of fast relaxation rare earth ion Dy³⁺With the purpose of illustrating Bi by comparison³⁺The effect on raising the dielectric constant, which does not significantly contribute to other parameters, andhe substituted ions had little effect on the dielectric constant.

Sintering temperature change specification: formula sintering temperature and oxide Bi of garnet type ferrite with high dielectric constant₂O₃The content of (A) is closely related, Bi₂O₃The sintering temperature can be greatly reduced, so in order to ensure that the sintering quality level of the ferrite prepared by the comparative example 1 is similar so as to carry out performance test comparison, the sintering temperature needs to be adjusted, and the sintering time is unified for more than 20 h.

Comparative example 2 (comparison likewise based on example 1)

The comparative example differs from example 1 in that it has the formula:

Y_{3-x-y-a-b-c-d-e-f}Bi_xLa_yLu_zGd_aNd_bSm_cDy_dCa_e+fSn_eZr_fFe_5-δ-e-fO₁₂where x is 0.8, y =0.1, z is 0, a is 0, b =0, c is 0, d =0, e =0.3, f =0, δ is 0.1, the preparation of the ferrite is carried out according to the process flow of example 1.

Description of the drawings: comparative example 2 compared to example 1, abolished the fast relaxation rare earth ion Dy³⁺By replacement of Bi with retention of Bi³⁺Substituted and nonmagnetic rare earth ion La³⁺The aim is to compare and illustrate the spin wave line width delta H of the fast relaxation rare earth ions_kThe promotion of (B) and (B) are also described³⁺For spin wave line width Δ H_kNo obvious effect and no obvious contribution of fast relaxation rare earth ions to the dielectric constant.

Comparative example 3 (comparison likewise based on example 1)

The comparative example differs from example 1 in that it has the formula:

Y_{3-x-y-a-b-c-d-e-f}Bi_xLa_yLu_zGd_aNd_bSm_cDy_dCa_e+fSn_eZr_fFe_5-δ-e-fO₁₂wherein x is 0.8, y =0, z is 0, a is 0, b =0, c is 0, d =0.005, e =0.3, f =0, δ is 0.1, iron was performed according to the process flow of example 3And (3) preparing an oxygen body, wherein the presintering temperature is changed to 1200 ℃, and the sintering temperature and the heat preservation time are changed to 1400 ℃ and more than 20 h.

Description of the drawings: compared with example 1, comparative example 3 has formula without nonmagnetic rare earth ion La³⁺Substitution of (1) with fast relaxing ion, rare earth Gd³⁺And Bi³⁺The purpose of substitution is to illustrate the effect of nonmagnetic rare earth ions in the material of the invention for improving Curie temperature by comparison, and to illustrate that the nonmagnetic rare earth ions do not contribute significantly to dielectric constant and spin wave line width. Likewise, since there is no Bi here₂O₃Therefore, the sintering temperature is also adjusted to be high, and the similar sintering level is ensured for comparison.

The ferrite prepared in the above examples 1 to 4 and comparative examples 1 to 3 was subjected to the relevant electromagnetic property test in the following manner:

saturation magnetization of ferrite material 4 pi Ms, spin wave line width delta H_kCurie temperature Tc, ferromagnetic resonance line width Δ H, and dielectric loss tan δ_εDielectric constant ε_rThe test results are shown in Table 1, tested according to GB/T9633-2012.

Performing phase analysis on the prepared material with X-ray diffraction analyzer (Panalytical X' Pert Powder, the Netherlands), wherein the XRD spectrum of the analysis result is shown in figures 1-4;

with respect to the drawings, it is to be explained that: examples 1 to 4 are composite ferrites having high dielectric constant and high power capability, so the drawings only show 1 to 4, because the ferrites of the examples are completely solid solution substituted, and there are no XRD characteristic peaks except for garnet phase in theory and test results, so the test XRD peak patterns of all the examples herein are similar, indicating that the substituted ions are not present in the ferrites obtained in the examples as other oxide impurity phases;

high power characteristics in the present invention as spin linewidth Δ H_kPerformance is shown by the conventional spin linewidth Δ H of the garnet_kTypically very small, < 2 Oe, ferrite Δ H of embodiments of the present invention_kMore than 5 Oe, the conventional garnet ferrite material only has one characteristic of high dielectric or high power, the material of the invention combines two characteristics of high power and high dielectric constant,and has good higher Curie temperature Tc to ensure that the environment applicable temperature of the material is higher and more stable.

TABLE 1 results of electromagnetic property test of examples and comparative examples

Numbering	ε	tanδ	ΔH（Oe）	ΔH_k（Oe）	4πM_s（G）	T_c（℃）
							Example 1	21.3	7.4×10^-5	21	5.3	1955	284
Example 2	23.5	9.2×10^-5	40	21	1950	279
							Example 3	26	1.0×10^-4	26	11.2	1824	282
Example 4	30.2	1.2×10^-4	32	15	1706	271
							Comparative example 1	14	1.6×10^-4	20	5.1	1950	280
Comparative example 2	22.1	1.0×10^-4	21	＜2	1983	274
							Comparative example 3	21.8	1.4×10^-4	24	5.3	1965	261

The comparison factors are three: bi³⁺Ions; magnetic rare earth ion Gd³⁺ 、Sm³⁺、Nd³⁺、Dy³⁺Wherein Sm³⁺、Nd³⁺、Dy³ ⁺Is a fast relaxation rare earth ion; non-magnetic rare earth ion La³⁺、Lu³⁺. The three types of ions respectively correspond to the ferrite performance and the dielectric constant epsilon_rSpin linewidth Δ H_kAnd adjusting and controlling the Curie temperature Tc.

Comparative example 1 formulation formula on the basis of example 1, Bi is eliminated³⁺In contrast to example 1, the absence of Bi₂O₃The sintering temperature is reduced, so that better ceramic sintering quality can be achieved at a high temperature of 1400 ℃; comparative example 1 shows the absence of Bi³⁺Dielectric constant epsilon of ferrite material after substitution_rReduced, does not have high dielectric constant performance, but has excellent spin linewidth and Curie temperature.

Comparative example 2 formula chemical formula fast relaxation rare earth ion Dy was cancelled based on example 1³⁺Instead, the spin linewidth Δ H of the ferrite material obtained in comparative example 2 is larger than that of example 1_kLower, without high power performance, but still with a high dielectric constant and a higher curie temperature.

Comparative example 3 formula chemical formula non-magnetic rare earth ion La was removed based on example 1³⁺Instead, the ferrite obtained in comparative example 3 has a decreased curie temperature compared to example 1, but still has high power performance characteristics and high dielectric constant performance.

The above embodiments further describe the technical solutions and advantageous effects of the present invention in detail, but it should not be construed that the specific implementations of the present invention are limited to these descriptions. Any modification, equivalent replacement, improvement and the like made by a person having ordinary skill in the art to which the present invention pertains without departing from the spirit of the present invention should be considered to be within the protection scope of the present invention.

Claims

1. A high-dielectric constant high-power microwave ferrite material is characterized in that the chemical formula is Y_{3-x-y-a-b-c-d-e-} _fBi_xLa_yLu_zGd_aNd_bSm_cDy_dCa_e+fSn_eZr_fFe_5-δ-e-fO₁₂Wherein x is more than or equal to 0.8 and less than or equal to 1.6, y + z is more than or equal to 0 and less than or equal to 0.2, a is more than or equal to 0 and less than or equal to 0.7, b + c is more than or equal to 0 and less than or equal to 0.06, d is more than or equal to 0.005 and less than or equal to 0.05, e + f is more than or equal to 0.25 and less than or equal to 0.55, delta is the iron deficiency, and delta is more than or equal to 0.03 and less than or equal to 0.1.

2. The method for preparing a high dielectric constant high power microwave ferrite material of claim 1, wherein: the method comprises the following steps:

(1) according to the chemical formula Y_{3-x-y-a-b-c-d-e-f}Bi_xLa_yLu_zGd_aNd_bSm_cDy_dCa_e+fSn_eZr_fFe_5-δ-e-fO₁₂Wherein x is more than or equal to 0.8 and less than or equal to 1.6, Y + z is more than or equal to 0 and less than or equal to 0.2, a is more than or equal to 0 and less than or equal to 0.7, b + c is more than or equal to 0.06, d is more than or equal to 0.005 and less than or equal to 0.05, e is more than or equal to 0.25 and less than or equal to 0.55, delta is the iron deficiency, delta is more than or equal to 0.03 and less than or equal to 0.1, and each raw material is calculated and weighed, wherein the raw material is Y₂O₃、Gd₂O₃、Dy₂O₃、Sm₂O₃、Nd₂O₃、La₂O₃、Lu₂O₃、Bi₂O₃、CaCO₃、SnO₂、ZrO₂、Fe₂O₃；

(4) performing wet ball milling for the second time, namely performing wet ball milling for the presintered powder obtained in the step (3) for the second time to obtain slurry of the presintered material;

3. The method of claim 2, wherein the purity of the raw material in step (1) is analytically pure.

4. The method according to claim 2, wherein the ball milling time in the step (2) is 4 to 6 hours.

5. The method of claim 2, wherein the binder in step (5) is an aqueous solution of polyvinyl alcohol (PVA) having a concentration of 5wt% to 15 wt%.