CN101255053B - High-temperature single-phase ferromagnetic-ferroelectric multiferroics ceramic material and preparation method thereof - Google Patents
High-temperature single-phase ferromagnetic-ferroelectric multiferroics ceramic material and preparation method thereof Download PDFInfo
- Publication number
- CN101255053B CN101255053B CN2008100357032A CN200810035703A CN101255053B CN 101255053 B CN101255053 B CN 101255053B CN 2008100357032 A CN2008100357032 A CN 2008100357032A CN 200810035703 A CN200810035703 A CN 200810035703A CN 101255053 B CN101255053 B CN 101255053B
- Authority
- CN
- China
- Prior art keywords
- phase
- ferroelectric
- perovskite structure
- ferromagnetic
- sosoloid
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Fee Related
Links
Images
Abstract
The invention discloses a high-temperature single-phase ferrimagnetic-ferroelectric multi-ferric ceramic material composition and a preparation method thereof. A ternary solid solution ceramics with a component scope of BiCrO3-BiFeO3-ABO3 is of a single-phase perovskite structure and the ferromagnetic and ferroelectric phase transition curie temperatures are as high as 460 K and can be adjusted along with the component change. According to the chemical pressure theory, a synthesis method of single-phase double perovskite oxide with a composition of Bi2CrFeO6 and a solid solution technique which enables Fe and Cr elements a highly-orderly distribution in B position of the perovskite structure. A ternary solid solution multi-ferric ceramics with a B-orderly single-phase perovskite structure of BiCrO3-BiFeO3-ABO3 is obtained by using the traditional solid state reaction electronic ceramic process, the solid solution technique and controlling the solid phase reaction order. The invention provides a new material basis for promoting prior industries to upgrade and foster new industries.
Description
Technical field
The invention belongs to material science, relate to magnetoelectricity multiferroic functional materials technology.
Background technology
Electronics and magneticsubstance have been penetrated into all respects of modern technologies and daily life.The trend of device miniaturization causes that people extraordinarily pay close attention to magnetic and Electronic Performance incorporated the multifunctional material of one, thereby makes the individual equipment assembly can carry out task more than one.Ferroelectric, ferromagnetic, iron bullet material is three kinds of important iron (ferroic) materials, is the important component part of present electronics and magnetic functional material family; And magnetoelectricity, piezoelectricity and magnetostriction materials are most important three members of multiferroic material (multiferroics) family, and the cross-coupling effect between electricity, magnetic or structure preface parameter and the regulation and control behavior that intersects are the cores [1-3] that the used components and parts of feedback were obtained, transmit, store and carried out to information in modern information technologies and the infosystem.At present, the multiferroic material in technical field widespread use is piezoelectric (as PZT, PVDF) and magnetostriction materials (as ferrite, Terfenol-D) and has produced huge economic benefit.Their electricity (magnetic) polar changes the change that is accompanied by shape, and vice versa, is usually used in the sound wave-electrical signal conversion of acoustical detector and the electricimpulse of driving mechanism-driving conversion, the annual market that produces the more than one hundred billion dollar.
Ferromagnetic-ferroelectric multiferroic material not only has double attribute ferromagnetic, ferroelectric material, and can produce cross-couplings between magnetic polarization and the electropolarization and intersect the new function of regulation and control, a wherein most important coupling effect is exactly an iron electric polarization to the response to external electric field of the response of external magnetic field and spin magnetic moment.Because magneto-electric coupled factor alpha and DIELECTRIC CONSTANT and magnetic permeability μ satisfy thermodynamics mean field theory relation: α
Ij 2＜ε
Iiμ
Jj, therefore ferromagnetic-ferroelectric multiferroic body has the maximum magnetic flux coupling effect [1,2] of expection.
The theory and practice of single-phase magnetoelectric material studies show that producing ferromegnetism and ferroelectric common micromechanism in the simple perovskite structure oxide is to repel mutually, and they need empty or partially filled transition metal track [3-5] respectively.At present, known single-phase magnetoelectricity multiferroic material system, the overwhelming majority is antiferromagnetism or weak parasitic ferromagnetism (inclination antiferromagnetism); Known (Asia) ferromagnetic-and ferroelectrics has only three classes, but they have at least a transformation temperature to be lower than 200K:1) boric spar Ni
3B
7O
13I, ferromagnetic phase transition Curie temperature Tc_M=60K, ferroelectric phase transition Curie temperature Tc_E=400K; 2) perovskite structure BiMnO
3, Tc_M=105K, Tc_E=750～770K; 3) Pb (Fe
2/3W
1/3) O
3, ferrous magnetic Tc_M=383K, Tmax_E=190K.High temperature high-insulativity single-phase magnetoelectricity multiferroic functional materials and device are the bases that leads generation information technology and equipment Manufacturing Technology Development, being the core component of intelligent material and intelligence structure, is to promote existing industrial upgrading and cultivate the basic substance of new industry.Therefore, development magnetoelectric material design theory and material preparation science and technology, designing and developing room temperature ferromagnetic-ferroelectric multiferroic material still is the primary goal that Condensed Matter Physics and materialogy research are pursued.
The main reference document:
1、N.A.Spaldin?and?M.Fiebig，Science?309，391(2005)
2、M.Fiebig，J.Phys.D38，R123(2005)
3、N.A.Hill，J.Phys.Chem.B?104，6694(2000)
4、N.A.Hill，A.Filippetti，J.Magn.Magn.Mater.242-245，976(2002)
5、P.Baettig，C.Ederer，and?N.A.Spaldin，Phys.Rev.B?72，214105(2005)
Summary of the invention
The objective of the invention is to start with from strong related physical theory, material design and experimental study three aspects, understand in in-depth analysis on the basis of the coexistence mechanism of iron preface parameters such as perovskite structure oxide self power generation polarization and spontaneous magnetization and temperature effect characteristic thereof, a kind of high temperature ferromagnetic-ferroelectric multiferroics monophase materials and preparation method thereof is provided.
For reaching above purpose, solution of the present invention is:
A kind of high temperature single-phase ferromagnetic-ferroelectric multiferroics stupalith, the sosoloid technological method of principle is pressed in utilization based on chemistry, (details of " sosoloid technological method " are that the industry those of ordinary skill is known promptly to adopt the element of different ions radius to substitute the technological method that forms single phase solid solution, PZT is exactly this example), realize the Bi that the Fe-Cr element distributes at perovskite structure B position high-sequential
2CrFeO
6The single-phase of structure of double perovskite oxide compound synthesized, and its chemical composition is: (1-x-y) BiCrO
3-xBiFeO
3-yABO
3: A=Pb wherein, Ba, Sr; B=Ti; X=0.3～0.7.y=0.1～0.4.
Further, described high temperature single-phase ferromagnetic-ferroelectric multiferroics stupalith, its component is specially: (1-x-y) BiCrO
3-xBiFeO
3-yPbTiO
3: x=0.45～0.50 wherein, y=0.25～0.30.
Prepare this high temperature single-phase ferromagnetic-ferroelectric multiferroics method of ceramic material one:
A, raw material are Bi
2O
3, Cr
2O
3, Fe
2O
3, PbO, BaO, SrO and TiO
2Oxide powder;
B, Bi
2O
3, Cr
2O
3, Fe
2O
3, PbO (BaO, SrO) and TiO
2Oxide powder is by (1-x-y) BiCrO
3-xBiFeO
3-yABO
3Proportioning weighing, wet-mixed, 900-1100 ℃ solid state reaction are synthesized;
C, granulation, binding agent is: 200ml deionized water-2gPVA-1ml glycerine-30ml ethanol, 200～250MPa pressure compressing tablet;
D, green sheet were 950～1050 ℃ of insulations 2～10 hours.
Prepare this high temperature single-phase ferromagnetic-ferroelectric multiferroics method of ceramic material two:
A, raw material are Bi
2O
3, Cr
2O
3, Fe
2O
3, PbO, BaO, SrO and TiO
2Oxide powder;
B, Bi
2O
3, Cr
2O
3, Fe
2O
3, PbO (BaO, SrO) and TiO
2Oxide powder is pressed 0.25BiCrO
3-0.30BiFeO
3-0.45ABO
3Proportioning weighing, wet-mixed, 900-1100 ℃ solid state reaction are synthesized;
C, 0.25BiCrO
3-0.30BiFeO
3-0.45ABO
3Ceramics powder and Bi
2O
3, Cr
2O
3, Fe
2O
3By (1-x-y) BiCrO
3-xBiFeO
3-yABO
3Proportioning weighing, wet-mixed, 900-1100 ℃ solid state reaction are synthesized.
D, granulation, binding agent is: 200ml deionized water-2gPVA-1ml glycerine-30ml ethanol, 200～250MPa pressure compressing tablet;
E, green sheet were 950～1050 ℃ of insulations 2～10 hours.
The BiCrO of (x=0.3～0.7, y=0.1～0.4) in certain compositional range
3-BiFeO
3-ABO
3The ternary solid solution pottery is single-phase perovskite structure.
Above-mentioned perovskite structure single phase solid solution oxide compound is the ferromagnetic-ferroelectric multiferroics body, and ferromagnetic and ferroelectric transition temperature all can be up to 460K, and adjustable with change of component.
Owing to adopted such scheme, the present invention to have following characteristics: the present invention adopts traditional electronic ceramic technology, adopts sosoloid technology and control solid state reaction order, obtains a kind of high temperature ferromagnetic-ferroelectric multiferroics pottery of single-phase perovskite structure.Principal feature comprises:
(1) develops a kind of high temperature ferromagnetic-ferroelectric multiferroics pottery;
(2) BiCrO in certain compositional range
3-BiFeO
3-ABO
3The ternary solid solution pottery is single-phase perovskite structure, is high temperature ferromagnetic-ferroelectric multiferroics body, and ferromagnetic and ferroelectric transition temperature is up to 460K and adjustable;
(3) experiment obtains BiCrO
3, BiFeO
3And ABO
3The partial phase diagram of the relevant structure of ternary system, performance and component relation;
(4) utilize chemistry to press principle,, realized Bi by the sosoloid technology
2CrFeO
6The single-phase of structure of double perovskite oxide compound synthesized, and realized that Fe-Cr (Ti) element distributes at perovskite structure B position high-sequential;
(5) adopt traditional electronic ceramic technology, technology is simple, by controlling the generation that the solid state reaction order has suppressed the pyrochlore structure phase, obtains the BiCrO of perovskite structure
3-BiFeO
3-ABO
3One-component ceramic.
Description of drawings
Fig. 1 adopts the conditional electronic ceramic process, and the single stage method solid state reaction is synthesized BiCrO
3-BiFeO
3-PbTiO
3Ternary solid solution XRD structure iron.2 θ=27.9 °, 53 ° show that with 55 ° of three diffraction peaks a small amount of pyrochlore structure second exists mutually.
Fig. 2 is different components BiCrO
3-BiFeO
3-PbTiO
3Spontaneous magnetic moment-the temperature relation of ternary solid solution pottery.This sample is the ferrous magnetic behavior of R type, and the ferromagnetic phase transition Curie temperature is adjustable with change of component.
Fig. 3 is x=0.50, the spontaneous magnetic moment-magnetic field dependence under the y=0.25 sample condition of different temperatures.Illustration is represented the spontaneous magnetic moment-temperature relation after magnetic moment-magnetic field dependence is measured preceding and measurement.
Fig. 4 is x=0.45, dielectric temperature spectrum under the y=0.30 sample different frequency condition.
Fig. 5 is x=0.45, the dielectric frequency spectrum under the y=0.30 sample room temperature condition.
Fig. 6 is x=0.45, the polarization-widely different line of voltage electric hysteresis under the different voltage conditions of y=0.30 sample room temperature.
Fig. 7 adopts the conditional electronic ceramic process, and the two-step approach solid state reaction is synthesized BiCrO
3-BiFeO
3-PbTiO
3Ternary solid solution XRD structure iron.2 θ=27.9 °, 53 ° and 55 ° of three diffraction peaks disappear and show that ternary solid solution is the single-phase of perovskite structure in XRD diffraction sensitivity range.
Embodiment
The following examples are to further specify of the present invention, rather than limit the scope of the invention.
1, single stage method BiCrO
3-BiFeO
3-PbTiO
3Pottery preparation: with Bi
2O
3, Cr
2O
3, Fe
2O
3, PbO and TiO
2Oxide powder (Japanese Wako chemistry) is pressed the stoicheiometry weighing, adds dehydrated alcohol and grinds 2 hours at agate mortar, 1000 ℃ of roasts 5 hours; Raw material are pulverized, and add dehydrated alcohol and grind 2 hours simple stress moulding, forming pressure 250MPa, green compact diameter 10mm at agate mortar; Green sheet is at 10 hours sintering of 1000 ℃ of insulations.X-ray diffraction measure sample principal crystalline phase is counterfeit cubic perovskite structure, has a small amount of pyrochlore structure second to exist mutually, and test result is seen Fig. 1.
Fig. 2 is different components BiCrO
3-BiFeO
3-PbTiO
3Spontaneous magnetic moment-the temperature relation of ternary solid solution pottery.Fig. 3 is x=0.50, the magnetic moment-magnetic field dependence of y=0.25 sample under condition of different temperatures.Illustration is represented the spontaneous magnetic moment-temperature relation after magnetic moment-magnetic field dependence is measured preceding and measurement.BiCrO in certain compositional range
3-BiFeO
3-PbTiO
3Ternary solid solution is a R type Ferrimagnetism, and the ferromagnetic phase transition Curie temperature is to x=0.50, and the y=0.25 sample is～460K to reduce BiFeO
3Or/and increase PbTiO
3Content all causes the system Curie temperature to reduce and spontaneous magnetization reduces.Simultaneously, the chaotic distribution of perovskite structure B position ion Fe and Cr (Ti) has also reduced the spontaneous magnetization of system, is about 20% by Fig. 3 measuring result estimation sample degree of disorder; The complete unordered system that will cause of Fe and Cr (Ti) is the spin glass body (spin glass) of antiferromagnetic coupling.
With x=0.45, y=0.30 sample ceramic plate polishing both surfaces is carried out dielectric properties and ferroelectric properties test behind silver, the silver ink firing.Fig. 6 provides under the different frequency condition dielectric frequency spectrum under dielectric temperature spectrum and the room temperature condition.Fig. 7 provides the different voltage conditions of the sample room temperature widely different line of polarization-voltage electric hysteresis down.Because the resistivity of sample is 10
6Europe centimetre magnitude, the dielectric meter reveals stronger Debye relaxation, and preliminary electrical measurement shows that sample is a relaxation ferroelectric.
2, two-step approach BiCrO
3-BiFeO
3-PbTiO
3Pottery preparation: with Bi
2O
3, Cr
2O
3, Fe
2O
3, PbO and TiO
2Oxide powder is pressed 0.25BiCrO
3-0.30BiFeO
3-0.45PbTiO
3The stoicheiometry weighing adds dehydrated alcohol and ground 2 hours at agate mortar, 1000 ℃ of roasts 5 hours, and structure is shown in A among Fig. 7; By 0.25BiCrO
3-0.30BiFeO
3-0.45PbTiO
3Ceramics powder and Bi
2O
3, Cr
2O
3, Fe
2O
3By the x=0.45 of institute, the weighing of y=0.30 proportioning, wet-mixed, simple stress moulding, forming pressure 250MPa, green compact diameter 10mm; Green sheet is at 10 hours sintering of 900-1000 ℃ of insulation.The X-ray diffraction measure sample is counterfeit cubic perovskite structure, and 1000 ℃ of sintering have not had pyrochlore structure second and existed mutually, and test result is seen Fig. 7, shown in the A+B.
The above-mentioned description to embodiment is can understand and apply the invention for ease of those skilled in the art.The person skilled in the art obviously can easily make various modifications to these embodiment, and needn't pass through performing creative labour being applied in the General Principle of this explanation among other embodiment.Therefore, the invention is not restricted to the embodiment here, those skilled in the art should be within protection scope of the present invention for improvement and modification that the present invention makes according to announcement of the present invention.
Claims (4)
1. high temperature single-phase ferromagnetic-ferroelectric multiferroics stupalith, it is characterized in that: component is: (1-x-y) BiCrO
3-xBiFeO
3-yPbTiO
3: x=0.45～0.50 wherein, y=0.25～0.30.
2. high temperature single-phase ferromagnetic-ferroelectric multiferroics stupalith according to claim 1 is characterized in that: should (1-x-y) BiCrO
3-xBiFeO
3-yPbTiO
3Pottery is single-phase perovskite structure.
3. the described method of ceramic material of preparation claim 1 is characterized in that: utilize the sosoloid technological method of pressing principle based on chemistry, promptly adopt the technological method of the element substitution formation sosoloid of different ions radius, realize Bi
2CrFeO
6The single-phase synthetic and Fe-Cr element of base structure of double perovskite oxide compound comprises at the sosoloid technological method that perovskite structure B position high-sequential distributes:
A, raw material are Bi
2O
3, Cr
2O
3, Fe
2O
3, PbO and TiO
2Oxide powder;
B, Bi
2O
3, Cr
2O
3, Fe
2O
3, PbO and TiO
2Oxide powder is by (1-x-y) BiCrO
3-xBiFeO
3-yPbTiO
3Proportioning weighing, wet-mixed, 900-1100 ℃ solid state reaction are synthesized.
4. the described method of ceramic material of preparation claim 1 is characterized in that: utilize the sosoloid technological method of pressing principle based on chemistry, promptly adopt the technological method of the element substitution formation sosoloid of different ions radius, realize Bi
2CrFeO
6The single-phase synthetic and Fe-Cr element of base structure of double perovskite oxide compound comprises at the sosoloid technological method that perovskite structure B position high-sequential distributes:
A, raw material are Bi
2O
3, Cr
2O
3, Fe
2O
3, PbO and TiO
2Oxide powder;
B, Bi
2O
3, Cr
2O
3, Fe
2O
3, PbO and TiO
2Oxide powder is pressed 0.25BiCrO
3-0.30BiFeO
3-0.45PbTiO
3Proportioning weighing, wet-mixed, 900-1100 ℃ solid state reaction are synthesized;
C, 0.25BiCrO
3-0.30BiFeO
3-0.45PbTiO
3Ceramics powder and Bi
2O
3, Cr
2O
3, Fe
2O
3By (1-x-y) BiCrO
3-xBiFeO
3-yPbTiO
3Proportioning weighing, wet-mixed, 900-1100 ℃ solid state reaction are synthesized.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2008100357032A CN101255053B (en) | 2008-04-08 | 2008-04-08 | High-temperature single-phase ferromagnetic-ferroelectric multiferroics ceramic material and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2008100357032A CN101255053B (en) | 2008-04-08 | 2008-04-08 | High-temperature single-phase ferromagnetic-ferroelectric multiferroics ceramic material and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN101255053A CN101255053A (en) | 2008-09-03 |
| CN101255053B true CN101255053B (en) | 2011-06-22 |
Family
ID=39890217
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN2008100357032A Expired - Fee Related CN101255053B (en) | 2008-04-08 | 2008-04-08 | High-temperature single-phase ferromagnetic-ferroelectric multiferroics ceramic material and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN101255053B (en) |
Families Citing this family (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP5681398B2 (en) * | 2009-07-09 | 2015-03-04 | 富士フイルム株式会社 | Perovskite oxide, ferroelectric composition, piezoelectric body, piezoelectric element, and liquid ejection device |
| GB201012637D0 (en) * | 2010-07-28 | 2010-09-15 | Univ Leeds | Ceramic |
| CN102086119B (en) * | 2010-12-09 | 2013-03-20 | 华中科技大学 | Method for preparing room-temperature multiferroic BiFeO3-SrTiO3 sosoloid ceramics |
| CN102173764B (en) * | 2011-01-11 | 2013-02-27 | 桂林理工大学 | Bismuth-ferrite-base multiferroic material and preparation method thereof |
| CN102584193B (en) * | 2012-02-02 | 2013-07-24 | 陕西科技大学 | Preparation method of bismuth ferrate barium titanate solid solution composite material with high magnetization intensity and high polarization intensity |
| CN103524129B (en) * | 2013-10-08 | 2015-03-04 | 江苏大学 | Piezoceramic material for ultrasonic emission-type transducers and preparation method |
| CN105355714B (en) * | 2015-11-06 | 2017-03-22 | 南京理工大学 | Double-layer perovskite film with ferroelectric and semiconductor photovoltaic effects |
| CN106810234B (en) * | 2017-01-18 | 2020-01-24 | 北京工业大学 | Single-phase multiferroic material with cubic perovskite structure |
| CN107892567B (en) * | 2017-11-03 | 2020-12-04 | 北京工业大学 | (Bi)1/2K1/2)TiO3Base binary leadless piezoelectric ceramic and preparation thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000169223A (en) * | 1998-11-30 | 2000-06-20 | Kyocera Corp | Piezoelectric ceramic composition and its production |
| CN101037338A (en) * | 2007-04-25 | 2007-09-19 | 上海大学 | Method for preparing ferrite bismuth lanthanum-titanate lead solid solution ceramic under strong magnetic field action |
-
2008
- 2008-04-08 CN CN2008100357032A patent/CN101255053B/en not_active Expired - Fee Related
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000169223A (en) * | 1998-11-30 | 2000-06-20 | Kyocera Corp | Piezoelectric ceramic composition and its production |
| CN101037338A (en) * | 2007-04-25 | 2007-09-19 | 上海大学 | Method for preparing ferrite bismuth lanthanum-titanate lead solid solution ceramic under strong magnetic field action |
Also Published As
| Publication number | Publication date |
|---|---|
| CN101255053A (en) | 2008-09-03 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101255053B (en) | High-temperature single-phase ferromagnetic-ferroelectric multiferroics ceramic material and preparation method thereof | |
| Sharma et al. | Structural, dielectric, ferromagnetic, ferroelectric and ac conductivity studies of the BaTiO3–CoFe1. 8Zn0. 2O4 multiferroic particulate composites | |
| Pradhan et al. | Room temperature multiferroic properties of Pb (Fe0. 5Nb0. 5) O3–Co0. 65Zn0. 35Fe2O4 composites | |
| Zhang et al. | Dielectric, magnetic and magnetoelectric properties of Ni0. 5Zn0. 5Fe2O4+ Pb (Zr0. 48Ti0. 52) O3 composite ceramics | |
| Xu et al. | The Study of Microstructure, Dielectric and Multiferroic Properties of (1− x) Co 0.8 Cu 0.2 Fe 2 O 4-x Ba 0.6 Sr 0.4 TiO 3 Composites | |
| Praveen et al. | Enhanced magnetoelectric coupling in Ti and Ce substituted lead free CFO-BCZT laminate composites | |
| Rawat et al. | Structural, dielectric, ferroelectric and magnetic properties of (x) CoFe 2 O 4-(1-x) BaTiO 3 composite | |
| Pattanayak et al. | A comparative study of structural, electrical and magnetic properties rare-earth (Dy and Nd)-modified BiFeO 3 | |
| Kanamadi et al. | Dielectric behaviour and magnetoelectric effect in (x) Ni0. 8Cu0. 2Fe2O4+ (1− x) Ba0. 9Pb0. 1Ti0. 9Zr0. 1O3 ME composites | |
| Pachari et al. | Improved magneto-capacitance response in combustion derived BaTiO3-(CoFe2O4/ZnFe2O4/Co0. 5Zn0. 5Fe2O4) composites | |
| Kulkarni et al. | Dielectric and magnetoelectric properties of (x) Ni0. 8Co0. 1Cu0. 1Fe2O4/(1− x) PbZr0. 8Ti0. 2O3 composites | |
| Chougule et al. | Studies on electrical properties and the magnetoelectric effect on ferroelectric-rich (x) Ni0. 8Zn0. 2Fe2O4+ (1− x) PZT ME composites | |
| Habib et al. | Enhancement of Piezoelectricity by Novel Poling Method of the Rare‐Earth Modified BiFeO3–BaTiO3 Lead‐Free Ceramics | |
| Wu et al. | Multiferroic ceramics in BaO–Y2O3–Fe2O3–Nb2O5 system | |
| Chauhan et al. | Crystal structure and improved dielectric, magnetic, ferroelectric and magneto-electric properties of x CoFe 2 O 4−(1− x) BaTiO 3 multiferroic composites | |
| Ai et al. | Synthesis and magnetoelectric properties of multiferroic composites of lead lanthanum zirconate titanate and mesoporous cobalt ferrite | |
| CN103030386B (en) | Multiferroic ceramics with room-temperature highly ferromagnetic-ferroelectric and highly-magnetic dielectric effects and preparation method of multiferroic ceramics | |
| Chougule et al. | Electrical conduction and magnetoelectric effect in ferroelectric rich (x) Ni0. 9Zn0. 1Fe2O4+(1− x) PZT ME composites | |
| Qin et al. | A comparative study on the dielectric and multiferroic properties of Co0. 5Zn0. 5Fe2O4/Ba0. 8Sr0. 2TiO3 composite ceramics | |
| Chougule et al. | Response of dielectric behavior and magnetoelectric effect in ferroelectric rich (x) Ni0. 9Zn0. 1Fe2O4+(1− x) PZT ME composites | |
| Singh et al. | Study of xCo0. 8Ni0. 2Fe2O4+ (1− x) Pb0. 99625 La0. 0025Zr0. 55Ti0. 45O3 magnetoelectric composites | |
| Chen et al. | Effect of mass ratio on the dielectric and multiferroic properties of Co 0.5 Zn 0.5 FeCrO 4/Ba 0.85 Ca 0.15 Zr 0.1 Ti 0.9 O 3 composite ceramics | |
| Rani et al. | Study of 0.1 Ni0. 8Zn0. 2Fe2O4− 0.9 Pb1− 3x/2LaxZr0. 65Ti0. 35O3 magnetoelectric composites | |
| Yao et al. | The effects of magnetic field and polarization on the permeability and permittivity of (1–x) Ni0. 4Zn0. 6Fe2O4+ xPb (Zr0. 53Ti0. 47) O3 composites at high frequency | |
| Kulkarni et al. | Magnetic and dielectric properties of Ni0. 8Co0. 1Cu0. 1Fe2O4+ PZT composites |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| C17 | Cessation of patent right | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20110622 Termination date: 20140408 |