WO2017058727A1 - Cold sintering ceramics and composites - Google Patents

Cold sintering ceramics and composites Download PDF

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Publication number
WO2017058727A1
WO2017058727A1 PCT/US2016/053772 US2016053772W WO2017058727A1 WO 2017058727 A1 WO2017058727 A1 WO 2017058727A1 US 2016053772 W US2016053772 W US 2016053772W WO 2017058727 A1 WO2017058727 A1 WO 2017058727A1
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WO
WIPO (PCT)
Prior art keywords
solvent
ceramic
inorganic compound
sintered
sintering
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.)
Ceased
Application number
PCT/US2016/053772
Other languages
English (en)
French (fr)
Inventor
Clive A. Randall
Jing Guo
Amanda BAKER
Michael Lanagan
Hanzheng Guo
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Penn State Research Foundation
Original Assignee
Penn State Research Foundation
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Priority to MX2018003476A priority Critical patent/MX2018003476A/es
Priority to EP24164739.5A priority patent/EP4365152A3/en
Priority to KR1020187011458A priority patent/KR102710637B1/ko
Priority to CN201680056988.0A priority patent/CN108137417B/zh
Priority to EP16852372.8A priority patent/EP3356310B1/en
Priority to CA2996051A priority patent/CA2996051C/en
Priority to JP2018536075A priority patent/JP6871257B2/ja
Priority to KR1020247031505A priority patent/KR20240147696A/ko
Application filed by Penn State Research Foundation filed Critical Penn State Research Foundation
Priority to US15/277,553 priority patent/US10730803B2/en
Publication of WO2017058727A1 publication Critical patent/WO2017058727A1/en
Anticipated expiration legal-status Critical
Priority to US16/905,236 priority patent/US11001530B2/en
Priority to US17/226,653 priority patent/US12077478B2/en
Ceased legal-status Critical Current

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    • C04B2237/34—Oxidic

Definitions

  • the present disclosure relates to sintering inorganic compounds, e.g., ceramics, with or without other substances, at low temperatures.
  • Ultra Low Temperature Cofired Ceramics are fired between 450 °C and 750 °C. See for example, He et al., "Low-Temperature Sintering Li 2 Mo0 4 /Nio.5Zno .5 Fe 2 0 4 Magneto-Dielectric Composites for High-Frequency Application", J. Am. Ceram. Soc. 2014:97(8): 1-5. Also Kahari et al.
  • An advantage of the present disclosure is a process to densify materials using a solvent and at a temperature around the boiling point of the solvent which is well below typical temperatures to sinter a material by many hundreds of degrees centigrade.
  • the processes of the present disclosure can use an aqueous based solvent and temperatures no more than 200 °C above the boiling point of the solvent.
  • a process for preparing a sintered material by combining at least one inorganic compound in particle form with a solvent that can partially solubilize the inorganic compound to form a mixture; and applying pressure and heat to the mixture to evaporate the solvent and densify the at least one inorganic compound to form the sintered material.
  • the applied heat is at a temperature of no more than 200 °C above the boiling point of the solvent.
  • Another aspect of the present disclosure includes a process for preparing a sintered composite, the process comprising combining at least one inorganic compound in particle form and at least one other substance with a solvent that can partially solubilize the inorganic compound to form a mixture; and applying pressure and heat to the mixture to evaporate the solvent and densify the at least one inorganic compound to form the composite.
  • the applied heat is at a temperature of no more than 200 °C above the boiling point of the solvent.
  • the other substance can be a different inorganic compound or it can be a polymer, metal or other material such as a glass or carbon fibers, for example.
  • the low temperature sintering of the present disclosure allows cold sintering of other substances that degrade or oxide at a temperature above 200 °C.
  • Another aspect of the present disclosure includes a process for preparing a sintered inorganic compound on a substrate.
  • the process includes depositing an inorganic compound (e.g., a ceramic) on a substrate (e.g., a substrate comprised of a metal, ceramic, polymer or combinations thereof).
  • the inorganic compounds can be deposited on multiple substrates to form laminates.
  • Solvent can be comnbined with the inorgainc compound before, during or after deposition thereof.
  • the process includes depositing an inorganic compound (e.g., a ceramic) on a substrate followed combining the inorganic compound with a solvent such as by exposing a deposited ceramic to an aqueous solvent to form a wetted deposited ceramic.
  • Heat and pressure can be applied to the wetted deposited ceramic to sinter the ceramic on the substrate.
  • the applied heat can be no more than 200 °C, the applied pressure no more than 5,000 MPa and the ceramic can be sintered to a relative density of no less than 85% in a short period of time.
  • Embodiments of the present disclosure include one or more of the following features individually or combined.
  • the cold sintering of the present disclosure is applicable to both inorganic compounds that have congruent dissolution and incongruent dissolution in the solvent.
  • the solvent can include one or more source compounds.
  • the at least one inorganic compound or ceramic can have a particle size of less than 100 ⁇ , or less than 50 ⁇ , 30 ⁇ , 20 ⁇ , 10 ⁇ , and even less than about 5 ⁇ or less than about 1 ⁇ and into the nanometer regime.
  • the solvent can include water with soluble salts and one or more of a Ci_i 2 alcohol, ketone, ester, and/or an organic acid with one or more soluble salts or source compounds wherein the solvent has a boiling point below about 200 °C.
  • the heat applied to the mixture is at a temperature below about 250 °C, e.g., below about 200 °C or below about 150 °C, such as below about 100 °C.
  • the inorganic compound and solvent can be combined by exposing the inorganic compound to a controlled relative atmosphere of the solvent, e.g., a humid atmosphere when the solvent is water based, or by mixing the solvent with the inorganic compound such as mixing a solvent that includes at least 50% by weight of water.
  • a controlled relative atmosphere of the solvent e.g., a humid atmosphere when the solvent is water based
  • mixing the solvent with the inorganic compound such as mixing a solvent that includes at least 50% by weight of water.
  • the cold sintering process of the present disclosure can advantageously provide dense sintered materials, e.g., dense inorganic compounds, ceramics, composites.
  • the process of the present disclosure can densify the material to a relative density of greater than 60%, e.g., greater than 80% such as no less than 85% and even greater than 90%.
  • the cold sintering process of the present disclosure can densify the sintered material in short time periods.
  • the cold sintering process of the present disclosure densifies the sintered material to a relative density of at least 85% and even at least 90% in less than 180 minutes, e.g., less than 120 minutes, such as no more than 60 minutes.
  • the cold sintering process of the present disclosure densifies the sintered material to a relative density of at least 85% and even at least 90% in no more than 30 minutes, for example.
  • Figure 1 illustrates a basic mechanism that can be used for a cold sintering process according to embodiments of the present disclosure.
  • the process is a basic, unique liquid phase sintering process that has not been exploited in the manufacture of sintered ceramic materials.
  • Figure 2 shows the basic diversity and integration for which cold sintering can be employed.
  • Figures 3a-3e are SEM micrographs of K 2 M0 2 O 7 in various forms. The figures show one example of microstructural development through varying processing conditions of time, temperature and pressure.
  • Figures 4a to 4c show densification trends for time, temperature and pressure variables.
  • Figures 4a to 4c are charts showing the relative densities of K 2 M0 2 O 7 ceramics sintered under various conditions.
  • Figure 4a is a chart of the relative densities of K 2 M0 2 O 7 ceramics sintered at 120 °C for 5 min with different pressures;
  • Figure 4b is a chart showing the relative densities of K 2 M0 2 O 7 ceramics sintered at a pressure of 350 MPa for 5 min with different temperatures;
  • Figure 4c is a chart showing the relative densities of K 2 M0 2 O 7 ceramics sintered at 120 °C at a pressure of 350 MPa with different holding times.
  • Figures 5a-5c are XRD patterns of cold-sintered bulk BaTi0 3 ceramic, and after annealing at 700-900 °C. Impurity phase -24° is outlined by the dash circle in (b).
  • Figure 5d is a TGA-MS plot for cold-sintered BaTi0 3 ceramic from 30-900 °C.
  • Figure 5e is a plot of density evolution of cold-sintered and subsequently annealed BaTi0 3 ceramics as a function of cold sintering time at 180 °C.
  • Figures 6a-6c are plots showing densities of: a) insulator-polymer (LM - PTFE), b) ionic conductor-polymer (LAGP - (PVDF-HFP)), and c) electronic conductor-polymer (V 2 O 5 - PEDOT:PSS) composites cold co-sintered at 120 °C.
  • LM - PTFE insulator-polymer
  • LAGP - ionic conductor-polymer
  • V 2 O 5 - PEDOT:PSS electronic conductor-polymer
  • Figures 7a-7e illustrate electrical and mechanical properties of LM - PTFE composites as a function of PTFE volume fraction.
  • Figure 7a is a plot of microwave permittivity
  • Figure 7b is a plot of Qxf values
  • Figure 7c is a plot of temperature coefficient of resonant frequency
  • Figure 7d is a plot of elastic modulus
  • Figure 7e is a plot of shear modulus.
  • Figures 8a- 8d illustrate electrical properties of ionic conductor-polymer (LAGP -
  • FIG. 8a is a plot of conductivities at 25 °C obtained from impedance measurements and Figure 8b is a plot of activation energies of LAGP - (PVDF-HFP) composites as a function of PVDF-HFP volume fraction before and after soaking in 1 M LiPF 6 EC-DMC (50:50 vol.%).
  • Figure 8c is a plot of DC conductivities at 25 °C and
  • Figure 8d is a plot of activation energies of V 2 0 5 - PEDOT:PSS composites as a function of PEDOT:PSS volume fraction.
  • Figures 9a-b are scanning electron micrographs of a cross-sectional view of a cold sintered Li 2 Mo04 in a single layered capacitor structure.
  • Figure 9a is a low magnification image of the dielectric cold sintered on PET film and
  • Figure 9b is a high magnification image with top and bottom silver electrodes.
  • Figure 10 is a plot comparing relative density to sintering temperature of inorganic materials (example BaTi0 3 ) made by different processes.
  • CS Conventional Sintering
  • TSS Two-Step Sintering
  • RCS Rate-Controlled Sintering
  • SPS Spark Plasma Sintering
  • MVS Microwave Sintering
  • HPS High Pressure Sintering
  • FS Flash Sintering
  • Combined RRS (Rapid-Rate Sintering)-RCS-LP (Low Pressure)- TSS
  • Sintering refers to a process that transforms a solid to a dense solid and typically includes thermal energy and/or pressure.
  • the present disclosure relates to cold sintering processes. That is, the present disclosure relates to processes to densify materials using a solvent that at least partially dissolves a component of the material and at a temperature within about the boiling point of the solvent and temperatures up to 200 °C above the boiling point (i.e., cold sintering).
  • the applied heat is at a temperature at the boiling point of the solvent and temperatures 50 to 80 °C above the boiling point.
  • the boiling point of the solvent is the boiling point at 1 atmosphere.
  • the sintering temperature is no more than 200 °C.
  • the process of the present disclosure can achieve dense solids at low temperatures across a wide variety of chemistries and composites.
  • the process includes combining at least one inorganic compound in particle form with a solvent that can partially solubilize the inorganic compound to form a mixture.
  • Other components e.g., other substances, can also be included with the inorganic compound.
  • the process sinters (e.g., densifies) the inorganic compound, with or without other components, by application of pressure and heat at a temperature to evaporate the solvent.
  • the application of pressure and heat at a temperature to evaporate the solvent advantageously causes the solvent to evaporate and densifies the inorganic compound, with or without other components, to form a densified material or composite.
  • the other substance is a substance that is different from the at least one inorganic compound.
  • the other substance can be a different inorganic compound or it can be a polymer, metal, or other material, for example.
  • Inorganic compounds useful for the present disclosure include, for example, ceramics, such as metal oxides, such as lithium metal oxides and non-lithium metal oxides, metal carbonates, metal sulfates, metal selenides, metal fluorides, metal tellurides, metal arsenide, metal bromides, metal iodides, metal nitrides, metal sulphides, metals and metal carbides.
  • ceramics such as metal oxides, such as lithium metal oxides and non-lithium metal oxides, metal carbonates, metal sulfates, metal selenides, metal fluorides, metal tellurides, metal arsenide, metal bromides, metal iodides, metal nitrides, metal sulphides, metals and metal carbides.
  • Fine powders for the at least one inorganic compound prior to forming the mixture advantageously gave better properties for the densified material.
  • Fine powders can be produced by milling the inorganic compound such as by ball milling, attrition milling, vibratory milling and jet milling, for example.
  • the at least one inorganic compound in particle form has a particle size of less than 100 ⁇ , or less than 50 ⁇ , 30 ⁇ , 20 ⁇ , 10 ⁇ , and even less than about 5 ⁇ or less than about 1 ⁇ .
  • Particle size can be determined by sedigraph methods, laser diffraction or equivalent methods in which at least 95% of the particles are at or below the stated particle size.
  • the temperature applied is no more than about 200 °C above the boiling point of the solvent. It is believed that the application of heat causes the solvent to evaporate, supersaturate the solubilized species and densifies the at least one inorganic compound to form the sintered material and/or composite.
  • the heat applied to the mixture is at a temperature below about 250 °C, e.g., below about 200 °C or below about 150 °C, such as below about 100 °C.
  • the materials of the present disclosure can be sintered under pressure of no more than about 5,000 MPa and preferably under an intermediate pressure, e.g., about 30 MPa to about 2,000 MPa, e.g., from about 250 MPa to about 750 MPa.
  • the pressure can be applied to aid cold sintering while the solvent can evaporate from the system.
  • Solvents useful in practicing the disclosure include one or more of a C 1-12 alcohol, ketone, ester, water and/or mixtures thereof.
  • Water can also be a solvent either alone or with one or more of a C 1-12 alcohol, ketone, or ester or mixtures thereof with or without a soluble salt.
  • Other components can be added to the solvent to adjust its pH, such as acidic components, including organic acids, e.g., citric acid, acetic acid, formic acid, nitric acid, oleic acid, etc.
  • the solvent can be an aqueous medium including water with optionally one or more soluble salts and optionally one or more C 1-12 alcohols, ketones, esters, and/or organic acids.
  • Embodiments include an aqueous solvent which includes at least 50% by weight of water and one or more other components such an organic acid or one or more of a Ci_ 12 alcohol, ketone, ester, or soluble salt or mixtures thereof.
  • the solvent has a boiling point below about 200 °C, e.g., below about 120 °C.
  • water and slightly acidic water can be added to the material in powder form before consolidation or afterwards in the form of water vapor.
  • Other solvents can be used to control the kinetics of the process, but water works sufficiently well in terms of practice.
  • the solvent can be combined with the inorganic compound and optional other components of the mixed with the inorganic compound by directly adding it to a prepared mixture of a fine powder of the inorganic compound and optionally other components or by exposing the inorganic compound and optional other components with vapor from the solvent.
  • the inorganic compound and optional other components can be under partial pressure during the addition of the solvent.
  • the solvent can simply be mixed in a small amount, e.g., less than about 30% by weight of the total solids such as less than about 0.3g/lg wt/wt, or by exposing the inorganic compound in powder form to a controlled relative atmosphere of the solvent such as exposing the inorganic compound to humid atmosphere for an aqueous solvent.
  • the cold sintering process densifies the material.
  • the relative density of the sintered material e.g., inorganic compound, ceramic or composite, is greater than 60%, e.g., greater than 80% such as no less than 85% and even greater than 90%.
  • the relative density of the sintered material is determined by Mass/Geometry ratio or Archimedes' method or an equivalent method.
  • the cold sintering process of the present disclosure densifies the sintered material in short time periods.
  • the cold sintering process of the present disclosure densifies the sintered material to a relative density of at least 85% and even at least 90% in less than 180 minutes, e.g., less than 120 minutes, such as no more than 60 minutes.
  • the cold sintering process of the present disclosure densifies the sintered material to a relative density of at least 85% and even at least 90% in no more than 30 minutes, for example.
  • the cold sintering process of the present disclosure is believed to be a low temperature liquid phase sintering process using a solvent, e.g., an aqueous medium, as a transient solvent.
  • a solvent e.g., an aqueous medium
  • a ceramic powder is uniformly moisturized with a small amount of solvent, e.g., an aqueous solution. It is believed that the solid surfaces of the ceramic powder decompose and partially dissolve in the solvent, so that a controlled amount of liquid phase is intentionally introduced at the particle- particle interfaces. This can be accomplished by simply mixing in a small amount, such as a few drops of the solvent, or exposing the powder to a controlled relative atmosphere of the solvent such as humid atmosphere for an aqueous solvent.
  • a subsequent growth stage is created through the evaporation of the solvent that enables supersaturated state of the liquid phase at a low temperature right above the boiling point of the solvent, e.g., right above 100 °C for an aqueous solvent, triggering a large chemical driving force for the solid and liquid phases to reach high levels of densification.
  • ceramics can be sintered at low temperature.
  • the process includes a ceramic in particle form that is exposed to a solvent, e.g., an aqueous solvent, in an amount of from 1 to 25wt% whereupon there is a partial dissolution of the ceramic to form a mixture, e.g., a particle bed.
  • a solvent e.g., an aqueous solvent
  • This particle bed with solvent can be exposed to a uniaxial pressure and under a controlled drying rate can provide particle rearrangement and precipitation to densify the particles and sinter to a dense ceramic, e.g., to a relative density of no less than 85%, such as greater than 90% in a short time period, e.g., less than 120 minutes such as 60 minutes or less.
  • Table 1 below shows materials that have already been demonstrated to undergo cold sintering according to the present disclosure.
  • the materials provided in Table 1 were cold sintered in accordance with the present disclosure to a density of no less than 80% and most of the materials were cold sintered in accordance with the present disclosure to a density of no less than 85%.
  • PZT materials such as PbZrTi0 3 can also be cold sintered.
  • the cold sintering processes disclosed herein can be applicable to arsenides, borides, bromides, carbonates, carbides, fluorides, metals, nitrides, oxides, phosphates, selenides, sulfides, tellurides, etc. with sufficient solubility in the solvent, and kinetics of re -precipitation from the transient supersaturated grain boundary phase is sufficiently fast relative to the heating rates.
  • Sintering of hydroxyapatite (HA) can also be undertaken by the present cold sintering processes disclosure herein.
  • laminated ceramics can be formed through the tape casting process and using low temperature binder systems, such as QPacTM, (polyalkylene carbonate) and its appropriate solvents and plasticizers. This can be used to cast the ceramic materials, and then these can be laminated. First, we can remove the binder at temperature 170 °C to 200 °C in air or nitrogen atmospheres. These materials can then carefully be exposed to high humidity to take up water in the surface of the particles. After a sufficient time, these unsintered laminates can be put in a uniaxial press and heated at 100 °C to less than 200 °C as a cold co-sintering process.
  • QPacTM polyalkylene carbonate
  • Figure 1 shows basic mechanisms for the cold sintering process according to certain embodiments.
  • the process is a basic, unique liquid phase sintering process that has not been exploited in the manufacture of ceramic materials.
  • Figure 2 shows the basic diversity and integration contemplated for cold sintering of the present disclosure.
  • Typical examples include microwave devices, electronic packages, and thermoelectric energy-conversion systems, as well as electrochemical systems, such as Li-ion batteries, where polymer separators and binders are interfaced with ceramic anode and cathode materials.
  • electrochemical systems such as Li-ion batteries
  • polymer separators and binders are interfaced with ceramic anode and cathode materials.
  • the impact would also be in systems that involve development of nanocomposites, and even simple monolithic applications, such as substrates, ceramic filters, and catalytic supports that could be processed at significantly lower temperatures with fast production times, enabling manufacturing to have higher throughput, cost- and energy-savings.
  • Figures 3a-3e illustrate microstructural development through varying processing conditions of time, temperature and pressure.
  • Figures 3a-3e are SEM micrographs of K 2 M0 2 O- 7 in various forms.
  • Figure 3(a) shows the K 2 M0 2 O- 7 powder
  • Figure 3(b) shows the K 2 M0 2 O 7 ceramic sintered at 120 °C for 5 min at a pressure of 350 MPa
  • Figure 3(c) shows the K 2 M0 2 O 7 ceramic sintered at 180 °C for 5 min at a pressure of 350 MPa
  • Figure 3(d) shows the K 2 M0 2 O 7 ceramic sintered at 120 °C for 15 min at a pressure of 350 MPa
  • Figure 3(e) shows the K 2 M0 2 O 7 ceramic sintered at 120 °C for 30 min at a pressure of 350 MPa.
  • Figures 4a to 4c show densification trends for time, temperature and pressure variables.
  • Figures 4a to 4c are charts showing the relative densities of K 2 M0 2 O 7 ceramics sintered under various conditions.
  • Figure 4a is a chart of the relative densities of K 2 M0 2 O 7 ceramics sintered at 120 °C for 5 min with different pressures;
  • Figure 4b is a chart showing the relative densities of K 2 M0 2 O 7 ceramics sintered at a pressure of 350 MPa for 5 min with different temperatures;
  • Figure 4c is a chart showing the relative densities of K 2 M0 2 O 7 ceramics sintered at 120 °C at a pressure of 350 MPa with different holding times.
  • the data in these figure show how time, temperature and pressure can affect cold sintering of a give system.
  • the amorphous-crystalline interface is typically arranged in a terrace-ledge manner, which is consistent with the classic Terrace-Ledge-Kink (TLK) model used to describe the equilibrium state of a crystal surface growing from the vapor or liquid; the terrace ends in a ledge and steps down to another one, and the missing atoms in the ledge forms kink sites.
  • TLK Terrace-Ledge-Kink
  • the step ledges and kinks provide energetically favorable sites for atomic diffusion and surface free energy minimization during liquid phase sintering, as the ionic species attached to these sites can establish a sufficient number of chemical bonds with the crystal surface so as to resist re-dissolving.
  • An advantage of cold sintering processes of the present disclosure includes the electrical properties of cold sintered Li 2 Mo0 4 , Na 2 Mo 2 0 7 , K 2 Mo 2 0 7 , and V 2 0 5 ceramics, which are comparable to those prepared by conventional thermal sintering at 540 °C, 575 °C, 460 °C, and 450-660 °C, respectively (Table 3, in the Examples section below).
  • the data demonstrates that many simple and mixed metal oxides, metal chlorides and composites in a number of crystal structures with a variety of different melting temperatures can be sintered between room temperature and 200 °C; certain of the cold sintered inorganic compounds are listed in Table 1.
  • Incongruent dissolution is prevalent in a large number of materials, and which also have limited solubility in aqueous media, especially for the close-packed structures in which the atoms/molecules/ligands are tightened by strong chemical bonding.
  • a well-known example is BaTi0 3 , which is not thermodynamically stable in aqueous environment of pH ⁇ 12. As BaTi0 3 particles react with water, Ba is preferentially leached out from the surface area, resulting in a Ba deficient layer with a Ti-rich amorphous shell. This amorphous layer is detrimental for the precipitation process since it separates the solution and crystal lattices and significantly impedes crystal growth from the supersaturated solution by limiting the mass transport between them.
  • inorganic compounds that would ordinarily incongruently dissolve in a solvent can be cold sintered, with or without other substances.
  • the process includes combining at least one inorganic compound in particle form with a solvent that can partially solubilize the inorganic compound to form a mixture.
  • the solvent is saturated or supersaturated with one or more source compounds prior to contacting the solvent with the inorganic compound.
  • the source compounds are preferable compounds that can synthesize the inorganic compound.
  • the source compounds are compounds that substantially prevent incongruent dissolution of the inorganic compound when in contact with the solvent.
  • Saturating to supersaturating the solvent with one or more source compounds prior to contact with the inorganic compound minimizes or prevents leaching of elements form the inorganic compound. It is believed leaching is due to the concentration difference between the solvent and the solid surface of the inorganic particles and adding the source compounds to the solvent to reach the concentration in saturate or supersaturation states prevents or minimizes leaching. While this aspect of the process of the present disclosure is particularly useful for inorganic compounds that incongruently dissolve in the solvent, it can be used for congruent dissolving compounds as well.
  • solvents including source compounds in the cold sintering process of the present disclosure is different from a process of combining reactive compounds to synthesize an inorganic compound in that the cold sintering process of the present disclosure starts with a fully synthesized inorganic compound and densifies the compound rather than to synthesize the compound from reaction components.
  • the process continues by applying pressure and heat to the mixture to evaporate the solvent and densify the at least one inorganic compound to form a sintered material or composite.
  • the applied heat in the embodiment is the same as in earlier embodiments, e.g., the applied heat is at a temperature of no more than 200 °C above the boiling point of the solvent or at a temperature below about 250 °C, e.g., below about 200 °C or below about 150 °C, such as below about 100 °C.
  • the at least one inorganic compound can include particles sized less than 100 ⁇ , or less than 50 ⁇ , 30 ⁇ , 20 ⁇ , 10 ⁇ , and even less than about 5 ⁇ or less than about 1 ⁇ .
  • a high relative density can be achieved in a short time period, e.g., a relative density of at least 85% and even greater than 90% can be achieved in less than 180 minutes, e.g., less than 120 minutes, such as no more than 60 minutes or no more than 30 minutes.
  • a process of cold sintering that includes using a solvent with source compounds, many ceramics that tend to dissolve incongruently in aqueous media can be sintered at low temperatures.
  • BaTi0 3 is a good material to demonstrate the advantages of cold sintering process of the present invention because: (1) it is a widely used ceramic material, particularly for multilayer ceramic capacitor (MLCC), (2) a dense BaTi0 3 ceramic is generally accomplished at -1200-1400 °C by conventional thermal sintering, and (3) compared to the micrometer-sized powder, BaTi0 3 nanoparticles are generally more chemically reactive due to their high surface energy.
  • MLCC multilayer ceramic capacitor
  • Figure 5a displays the phase structure evolution of as -cold- sintered BaTi0 3 ceramics and after post annealing at 700 - 900 °C. Further details within a specific angular range are also magnified as Figures 5b and 5c for better illustration.
  • impurity phase is identified, as circled by the dash line ( Figure 5b). It has been commonly reported that BaC0 3 generally appears as a by-product during hydrothermal synthesis of BaTi0 3 since a certain amount of barium species react with C0 2 at certain temperatures.
  • Figure 5d illustrates the thermogravimetric property of the cold-sintered ceramic during annealing process. Even though only a slightly total weight loss of ⁇ 1.8% is observed, sharp changes can still be detected at different temperature stages, and this can be more easily identified when a weight loss derivative with respective to the temperature is considered, as marked by peaks PI - P4. With the assistance of mass spectrum, these peaks perfectly correlate with the burning out of two chemical species, the OH " (or H 2 0) and C0 2 . Firstly, the water vapor comes off at ⁇ 100 °C, which might be attributed to the water detachment from the surface areas of ceramic powders.
  • BaTi0 3 nanoparticles are first homogeneously wetted with the water suspension containing the constituents for hydrothermal synthesis of BaTi0 3 .
  • the liquid phase redistributes itself and fills into the pores between the particles, aiding particle compaction and rearrangement. Raising up the temperature facilitates the hydrothermal reactions to generate a glass phase, and also speeds up the partial dissolving of BaTi0 3 surfaces into the solution, resulting in a round shape of the crystallite.
  • the shape of the crystallite accommodates: a rounded configuration is generally manifested when the glass phase is prevalent, while polyhedron with flat facets is normally developed when the volume of glass phase is significantly reduced. Simultaneously, mass transport during this process minimizes the excess free energy of the surface area and removes surface and porosity; the areas of crystallite-crystallite contacts increase, leading to a formation of rigid particulate skeletal network, and also resulting in a further improvement of the density to ⁇ 95% relative dense.
  • the other one is the “dissolution-precipitation mechanism", which suggests that Ti0 2 particles first dissolve into the aqueous solution to generate amorphous hydroxytitanium complexes (Ti(OH) n ⁇ ), and then react with dissolved barium to precipitate BaTi0 3 homogeneously from the solution/glass environment.
  • Ti element is found to be uniformly distributed into the glass phase. From this point of view, it seems to suggest that the presented cold sintering process most likely takes place via the dissolution- precipitation path aided by the epitaxial growth on BaTi0 3 particles.
  • the processes of cold sintering of the present disclosure are applicable to preparing composites of sintered inorganic compounds, e.g. ceramics, with polymers.
  • Co- sintering ceramic and polymers, e.g., thermoplastic polymers to form composites in a single step with very high volume fractions of ceramics seems unlikely, given the vast differences in the typical sintering temperatures of ceramics versus polymers.
  • these processing limitations can be overcome with the sintering processes of the present disclosure.
  • composites including one or more sintered inorganic compounds with one or more polymers can be formed.
  • the process includes combining at least one inorganic compound in particle form with at least one polymer and a solvent that can partially solubilize the inorganic compound to form a mixture.
  • the process continues by applying pressure and heat to the mixture to evaporate the solvent and densify the at least one inorganic compound to form a sintered material or composite.
  • the applied heat in the embodiment is the same as in earlier embodiments, e.g., the applied heat is at a temperature of no more than 200 °C above the boiling point of the solvent or at a temperature below about 250 °C, e.g., below about 200 °C or below about 150 °C, such as below about 100 °C
  • the at least one inorganic compound can include a certain percentage of particles sized less than 100 ⁇ , or less than 50 ⁇ , 30 ⁇ , 20 ⁇ , 10 ⁇ , and even less than about 5 ⁇ or less than about 1 ⁇ .
  • a high relative density of the inorganic compound can be achieved in a short time period, e.g., a relative density of at least 85% and even greater than 90% can be achieved in less than 180 minutes, e.g., less than 120 minutes, such as no more than 60 minutes or 30 minutes.
  • Table 2 below provides an exemplary list of thermoplastic polymers suitable for cold sintering according to embodiments of the present disclosure.
  • the sintering conditions of the present disclosure make it possible to co-sinter polymers and ceramic materials in a one-step sintering process.
  • Three illustrative examples include: microwave dielectric Li 2 Mo0 4 - (-C 2 F 4 -) n (PTFE), electrolyte Lii sAlo .
  • Dense Li 2 Mo0 4 (LM), Lii. 5 Alo. 5 Gei. 5 (P0 4 )3 (LAGP) and V 2 0 5 ceramics can be cold sintered at 120 °C for 15-60 minutes, as shown in Figure 6a-c, in contrast to high conventional thermal sintering temperatures and long holding times at 540 °C for 2 hours, 825 °C for 8 hours, and 450-660 °C for 2 to 26 hours, respectively.
  • the polymer is a light weight material, and thereby the densities of the ceramic-polymer composites decrease with increasing amount of polymer (Figure 6a-c).
  • the polymers were specifically selected to compliment the properties of the ceramic materials.
  • PTFE is a very good dielectric material
  • PVDF-HFP is an excellent host for Li-salts in polymer gel electrolytes
  • PEDOT:PSS is a good electronic conducting polymer.
  • the relative densities of all the ( 1 -x) LM - x PTFE and ( 1 - x) V 2 0 5 - x PEDOT:PSS samples are higher than 90%, and the densities of (1-x) LAGP - x (PVDF-HFP) samples range between 80 to 88%, indicating that the ceramic-polymer composites can be sintered well by a cold sintered process.
  • the PEDOT:PSS is a hydrophilic polymer with a pH value around 1.5- 2.5 in aqueous solution (3-4% PEDOT:PSS).
  • the lower pH value of PEDOT:PSS can enhance the dissolution rate of V 2 0 5 in water and slightly improve the relative density of (1-x) V 2 0 5 - x PEDOT:PSS composites.
  • the performance of ceramic-polymer composites depends on the properties of the component materials, their volume fractions, phase connectivity, particle sizes, porosity, etc. Dense ceramic-polymer composites can be obtained by cold sintering according to the present disclosure. Therefore, by changing the amount of polymer, it is possible to design the properties of ceramic-polymer composites, such as electrical and mechanical properties, as illustrated in Figure 7a.
  • the microwave dielectric (electrical) properties of (1-x) LM - x PTFE composites as a function of x value are plotted in Figure 7b-d.
  • the permittivity of PTFE is lower than that of Li 2 Mo0 4 , so that the relative permittivity of composites decrease from 5.8 to 2.9, with x increasing from 0 to 0.7.
  • a number of models have been proposed to predict the average permittivity of two-phase or multi-phase composites. The simplest model is assuming that the composite materials are aligned parallel and perpendicular (series) to the electric field, which derives the upper bound (Equation 1) and lower bound (Equation 2) of the relative permittivity of the composite, ⁇ , respectively:
  • ⁇ and ⁇ 2 are relative permittivities of phase 1 and phase 2, respectively;
  • the measured relative permittivity of (1-x) LM - x PTFE composites are lower than the calculated ones obtained from parallel mixing law and higher than that calculated from series mixing law.
  • the assumption of either perfectly parallel or perpendicular alignment is not appropriate for the real samples, and many modified models are deduced.
  • the relative premittivity of the composite can be derived from the principles of statistics:
  • Equation 3 V j Ei + ⁇ 2 ⁇ ⁇ 2 (-l ⁇ n ⁇ l) (3) [0073]
  • Equation 3 gives the expression of logarithmic mixing law:
  • Figure 7a shows that the measured permittivity data are in good agreement with the trends predicted by Equation 4.
  • Quality factor (Q), the reciprocal of loss tangent (Q l/tan5) is an important parameter to denote the energy loss of the microwave system.
  • Figure 7c shows that the Qxf (f, resonant frequency) value has no obvious deterioration when the amount of PTFE changes, indicating that the (1-x) LM - x PTFE composite can be used for microwave application.
  • LM and PTFE have different TCF values, therefore, with x increasing from 0 to 0.7, the TCF value of (1-x) LM - x PTFE composites shift from -170 to -7.2 ppm °C _1 ( Figure 7d). This result reveals that the thermal stability of resonate frequency of LM can be improved by adding PTFE.
  • a simple assumption to predict the TCF values of composites is the linear mixing rule, which is derived from the logarithmic mixing law of permittivity:
  • TCF Vi TCFi + V 2 TCF 2 (5)
  • TCF 2 TCF values of phase 1 and phase 2, respectively. It is seen that the experimental TCF values are similar to the predictions of Equation 5.
  • Polymers are relatively soft materials compared to ceramics which are stiff materials, so that the elastic and shear moduli of the (1-x) LM - x PTFE composites decrease with increasing PTFE content, as shown in Figure 7e. Similar to the prediction of permittivity, there are numerous models to calculate elastic/shear modulus of composites. The upper and lower bounds can be determined assuming that the composite materials are aligned parallel and perpendicular (series) to the direction of loading, respectively. Generally, the modulus lies between the upper and lower bounds, as demonstrated in Figure 7e. Here again using the logarithmic mixing rule, the measured modulus of composites has good agreement with the calculated one.
  • PTFE When the amount of PTFE is large, the measured modulus is a little smaller than that of calculated one. In this region, PTFE can be considered as the matrix and the ceramic is the filler. Many other models can be used to predict the modulus of (1-x) LM - x PTFE composites.
  • Amorphous regions of the PVDF-HFP copolymer absorb liquid electrolyte when soaked. Therefore, composite electrolytes were soaked in liquid electrolyte to boost ionic conductivity.
  • Conductivities at 25 °C of (1-x) LAGP - x (PVDF-HFP) composites soaked in 1 M LiPF 6 EC-DMC (50:50 vol.%) ranged from 3.3 x 10 "5 to 1.4 x 10 "4 S cm “1 , while activation energies ranged from 0.28 to 0.43 eV ( Figures 8a and 8b).
  • Well-crystallized, conventionally sintered LAGP has a conductivity of 3 x 10 "4 S cm "1 at 25 °C.
  • the total activation energy of cold sintered LAGP with and without polymer is consistent with a partially amorphous grain boundary (0.60 eV). Grain boundaries dominate the total conduction and total activation energy of cold sintered LAGP with and without polymer. In contrast, well-crystallized, conventionally sintered LAGP grain and grain boundary regions have similar activation energies (0.40 ⁇ 0.02 eV).
  • Literature describes the origin of grain boundary resistance to be geometrical current constriction from limited grain boundary contact area. While co-sintering ceramic with polymer may physically bridge resistive grain boundaries, soaking the composite in liquid electrolyte is required to ionically bridge these resistive grain boundaries. Polymer swelling through liquid electrolyte uptake also increases grain boundary contact area.
  • compositions with polymer loadings > 30 vol.%, where polymer swelling changes the composite dimensions, has been reported in flexible, solvent cast composites. After sixty days of soaking in liquid electrolyte at room temperature, dimensions of composite electrolytes of x ⁇ 0.30 in (1-x) LAGP - x (PVDF-HFP) did not change. No change in composite electrolyte dimensions is related to the cold sintered ceramic constraining the polymer's swelling.
  • V 2 0 5 is a wide bandgap semiconductor, which has an electronic DC conductivity
  • the DC conductivity of (1-x) V 2 0 5 - x PEDOT:PSS composites can be increased by 1-2 orders only by adding up to 1-2% PEDOT:PSS.
  • the activation energy of (1-x) V 2 0 5 - x PEDOT:PSS (0.8 ⁇ x ⁇ 0.27) composites is in the range of 0.22-0.23 eV, and lower than that of pure V 2 0 5 ceramic ( Figure 8d).
  • ceramic - polymer composites can be prepared using cold sintering processes of the present disclosure.
  • the composites can include a wide range of polymers and can be sintered to high densities by a low sintering temperature (e.g., as low as 120 °C) and for short time periods (e.g., ranging from 15-60 minutes).
  • the electrical and mechanical properties of composites can be predicted by the mixing law.
  • the cold sintering processes of the present disclosure can bridge the processing gap of ceramics and polymers, and open up a simple and effective way for material systems and devices using ceramics and polymers that are traditionally incompatible. Typically, hundreds of degrees separate the ability to co-process these materials in one step with high volume fractions of ceramic materials.
  • the cold sintering processes of the present disclosure allows fabrication of sintered materials and composites that include a substance that degrades or oxides at a temperature above about 200 °C.
  • Cold sintering allows for the fabrication of new materials and devices due primarily to its the low temperature process.
  • the cold sintering process of the present disclosure allows densification of different materials such as ceramics, polymers and metals on the same substrate to obtain functional circuitry.
  • Such materials and devices can be fabricated by depositing a ceramic, such as a ceramic paste, with or without other substances, on to a substrate (e.g., a substrate comprised of a metal, ceramic, polymer).
  • the substrate can have an electrode layer between the deposited ceramic and substrate among other device layers.
  • the ceraminc can be combined with a solvent such as by exposing the deposited ceramic to an aqueous solvent to form a more or less uniformily wetted deposited ceramic.
  • Heat and pressure can then be applied to the deposited and wetted ceramic to sinter the ceramic on the substrate in the same manner as heat and pressure were described for other embodiments.
  • the process can be heated to less than 200 °C, e.g., less than 150 °C, with a pressure of no more than 5,000 MPa, e.g., less than 2,000 Mpa, or between about 30 Mpa to about 1,000 MPa.
  • the sintered ceramic on the substate can achieve a relative density of greater than 80% such as no less than 85% and even greater than 90%.
  • the high relative density of the ceramic can be achieved in a short time period, e.g., a relative density of at least 85% and even greater than 90% can be achieved in less than 180 minutes, e.g., less than 120 minutes, such as no more than 60 minutes and even no more than 30 minutes. Fabrication of cold sintered capacitors on both metal and polymeric substrates are provided in the examples below.
  • Li2Mo04, Na2Mo207, K2M02O7 and Li2W04 powders were synthesized by the solid state reaction method using stoichiometric amounts of Li2C03, Na2C03, K2CO3, M0O3 and WO3. Mixtures of raw materials were milled with zirconia balls in ethanol for 24 h. After being dried, the powders were calcined in air at 450-600 °C, followed by a second ball mill with Zr02 and ethanol for 24 h.
  • Li2Mo04 powders were mixed with BaFel20l9, PTFE, and E- glass fibers (abbreviated as "EG") according to the following formula: O.8L12M0O4- 0.2BaFei2Ol9, 0.5Li2MoO4-0.5PTFE, and O.8L12M0O4-O.2EG (Volume Fraction).
  • EG E- glass fibers
  • the mixtures were ball milled in ethanol and then dried.
  • the particle sizes for these materials were accessed with SEM Scanning electron microscopy and the particle sizes were in the range of 0.5 to 10 microns.
  • B12O3, CsBr, L12CO3, CsS04, L12M0O4, Na2Mo207, K2M02O7, ZnMoCH, Gd2(Mo04)3, L12WO4, Na2W04, L1VO3, B1VO4, AgV03, Na2Zr03, LiFeP04, and KH2PO4, and dense composites of Li2Mo04-BaFel20l9, L12M0O4-PTFE, and L12M0O4-EG were prepared via the following methods including a cold-sintering step.
  • Method 1 All the powders except ZnO were mixed with 4-25 wt% deionized water using a pipet. ZnO was mixed with an aqueous acetic acid solvent with concentration of 0.5 - 5.0 M acetic acid (pH value of about 2-4). After being stirred with a mortar and pestle, the moistened powders were hot-pressed with a steel die into dense pellets (12.7 mm in diameter and 1-5 mm in height) under a uniaxial pressure of 80-570 MPa at 120 °C. The die was preheated at 120 °C for more than lh. Finally, the pellets were placed into an oven at 120 °C for 6h to remove the possibility of water residue.
  • Method 2 All the dry powders were pressed into soft pellets under a low pressure (30-70 MPa) at room temperature. Then, the pellets were put in a humid atmosphere (water vapor generated by heating deionized water or humidity chamber) for 10 ⁇ 360min. The moistened pellets were hot-pressed with a steel die into dense pellets under a uniaxial pressure of 80-570 MPa at 120 °C. The die was preheated at 120 °C for more than lh. Finally, the pellets were placed into an oven at 120 °C for 6h to remove the possibility of water residue.
  • a humid atmosphere water vapor generated by heating deionized water or humidity chamber
  • Multilayer Ceramic Preparation L12M0O4 and K2M02O7 tapes were prepared by the tape casting procedure. The powders were first added into a solution of 96wt% methylethylketone (MEK) and 4wt% Qpac, and milled with zirconia balls. Then, another solution of 66.3wt% methylethylketone (MEK), 28.4wt% Qpac and 5.3wt% Santicizer-160 was added into the slurry, followed by an additional ball milling. Tape casting was performed using a laboratory-type casting machine with a doctor blade casting head. Silicone-coated mylar (polyethylene terephthalate) was used as a carrier film.
  • MEK 96wt% methylethylketone
  • Qpac 66.3wt% methylethylketone
  • Santicizer-160 66.3wt% methylethylketone
  • Tape casting was performed using a laboratory-type casting machine with a doctor
  • Li2Mo04-K2Mo207 multilayer Li2Mo04 and K2M02O7 green tapes were stacked alternately.
  • Li2Mo04-Ag multilayer silver paste was printed on the Li2Mo04 green tape and two silver-printed layers and ten Li2Mo04 layers were stacked together. Then, the stacked Li2Mo04-K2Mo207 and Li2Mo04-Ag layers were laminated under an isostatic pressure of 20 MPa at 80 °C for 20 min. The binders were burn out at 175 °C for lOh in air with a heating rate of 0.5 °C /min.
  • the multilayers were sintered using a cold-sintering fabrication step, as described previously.
  • the multilayers were put in a humid atmosphere (water vapor generated by heating deionized water or humidity chamber) for 10 ⁇ 360min.
  • the moistened multilayers were hot-pressed with a steel die into dense ceramics under a uniaxial pressure of 80-570 MPa at 120 °C.
  • the die was preheated at 120 °C for more than lh.
  • the co-fired multilayers were placed into an oven at 120 °C for 6h to remove the possibility of residual hydroxides.
  • the bulk densities of the sintered samples were measured by Mass/Geometry ratio and Archimedes' method. Relative densities were determined by the ratio of experiment measured bulk density over the density of corresponding density of the materials in the form of single crystals.
  • Table 3 below provides densities and performance characteristics for certain ceramics prepared with a cold sintering step including water as a solvent and at 120 °C under a pressure of 350 MPa.
  • ⁇ ⁇ microwave permittivity.
  • tan5 loss.
  • f resonate frequency.
  • Ba(OH) 2 /Ti0 2 suspension was made by mixing corresponding chemicals with deionized water. The molar ratio of Ba(OH) 2 :Ti0 2 was 1.2: 1, and the concentration of Ba(OH) 2 was 0.1 mol L "1 .
  • 0.14 - 0.15 g Ba(OH) 2 /Ti0 2 suspension was added to 0.56 g BaTi0 3 nanopowders; the mixtures were grinded using pestle and mortar for 3 minutes.
  • the mixture was uniaxially pressed under 430 MPa first at room temperature (25 °C) for 10 minutes, and then the temperature was ramped up to 180 °C with an overall rate of 9 °C min "1 .
  • the temperature was isothermally kept for 1 minute to 3 hours to obtain a series of samples.
  • the as-prepared ceramic pellets were first baked at 200 °C overnight to further remove possible water residue, and then further annealed at 700 - 900 °C for 3 hours with a temperature ramp rate of 5 °C min "1 in air.
  • the densities were measured by Archimedes method using acetone (0.791 g cm " ) as a liquid media.
  • phase structures were checked by X-ray diffraction (Panalytical, X'Pert
  • the specimens were polished down to -30 ⁇ thick, and then mounted on molybdenum grids.
  • the foils were further thinned with an Ar-ion mill (Gatan, PIPS II) until an electron transparent perforation was formed.
  • a cryogenic stage was used to cool the specimen to the liquid N 2 temperature during ion milling to minimize structural damage and artifacts.
  • Microstructural and chemical studies were performed on a Talos (FEI, Talos) microscopy equipped with an Energy Dispersive X-ray Spectroscopy (EDS) system operating at an accelerating voltage of 200 kV.
  • EDS Energy Dispersive X-ray Spectroscopy
  • Li] .5 Alo .5 Ge].5(P0 4 )3 powder preparation Stoichiometric amounts of Li 2 C0 3
  • Alfa Aesar 99%
  • A1 2 0 3 Tepe Casting Warehouse, Inc.
  • Ge0 2 Alfa Aesar, 99.98%)
  • NH 4 H 2 P0 4 Alfa Aesar, 98%) were ball milled for 24 h, calcined in air at 750 °C for 30 min, and again ball milled for 24 h.
  • Milled powder was placed in a covered alumina crucible and melted in air at 1380 °C for 1 h before being splat-quenched.
  • Splat-quenched glass was annealed at 450 °C for 3.75 h and crystallized in air at 825 °C for 8 h.
  • Glass-ceramic powder was sieved through a 74 ⁇ mesh.
  • LAGP and PVDF-HFP were mixed by swirling in liquid nitrogen and pressed under 400 MPa uniaxial pressure at 120 °C for 1 h.
  • (1-x) V 2 0 5 - x PEDOT:PSS moistening took place with deionized water (11 to 17 wt.%) and dense ceramic- polymer composites were pressed under a uniaxial pressure of 350 MPa at 120 °C for 20-30 min.
  • TCF resonant frequency
  • a ceramic ink was prepared using Lithium Molybdenum Oxide powder (99+%,
  • a printing vehicle was made by mixing QPAC 40 (poly(propylene carbonate)) resin (Empower Materials, New Castle, DE) with Ethylene Glycol Diacetate (97%, Alfa Aesar, Ward Hill, MA) in amounts of 15 and 85 wt% respectively in a planetary centrifugal mixer (AR250, Thinky USA, Website, CA) until the resin was completely dissolved in the solvent.
  • QPAC 40 poly(propylene carbonate) resin
  • Ethylene Glycol Diacetate 97%, Alfa Aesar, Ward Hill, MA
  • Li 2 Mo04 the printing vehicle
  • additional ethylene glycol diacetate and Butyl Benzyl Phthalate S-160 (Tape Casting Warehouse, MorrisviUe, PA) in amounts of 66.1, 22.0, 11.0, and 0.9 wt% respectively were blended and homogenized in the planetary centrifugal mixer.
  • Substrates were prepared by cutting PET (Polyethylene terephthalate) sheets
  • a double pass was used for each printed layer of the double-layered prints, where the ink was dried at 120°C for 15 minutes between layers. Ceramic ink was also printed onto the Nickel Foil substrates using a 25.4 by 25.4 mm square pattern, 200 mesh screen as described above. Single layered prints were dried as above. Binder burnout was performed at 0.2 °C/min to 150 °C for the Nickel samples, and 175°C for the PET samples, with a dwell at peak temperature for 6 hours. [00103] Cold Sintering was performed by first exposing the printed samples to water vapor in a sealed beaker at 35-40°C until the bright white prints just turned a dull gray color, which indicated that water had absorbed into the printed ink squares.
  • Cold sintered printed Li 2 Mo0 4 capacitors have electrical and microstructural properties that are similar to those that have been conventionally processed.
  • the ability to co- process incompatible materials systems, such as low temperature polymers with high temperature ceramics, allows production of variety of new composites for device construction.
  • energy and time savings by employing the cold sintering method are significant when compared to conventional sintering methods.
  • Figure 10 is a plot comparing relative density to sintering temperature of inorganic materials (example BaTi0 3 ) made by different processes.
  • CS Conventional Sintering
  • TSS Two-Step Sintering
  • RCS Rate-Controlled Sintering
  • SPS Spark Plasma Sintering
  • MVS Microwave Sintering
  • HPS High Pressure Sintering
  • FS Flash Sintering
  • Combined RRS (Rapid-Rate Sintering)-RCS-LP (Low Pressure)- TSS

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Cited By (9)

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Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH038752A (ja) 1989-06-02 1991-01-16 Toyota Central Res & Dev Lab Inc 粘土鉱物焼結体およびその製造方法
JPH107411A (ja) 1996-06-20 1998-01-13 Nakamichi Yamazaki 含水物質の焼結方法、リン酸塩固化体、炭酸カルシウム固化体及びそれらの製造方法
JP2004115297A (ja) 2002-09-25 2004-04-15 Shiraishi Kogyo Kaisha Ltd ハイドロキシアパタイト多孔質燒結体の製造方法
US20040159390A1 (en) * 2001-10-01 2004-08-19 Heraeus Incorporated Methods for making and using self-constrained low temperature glass-ceramic unfired tape for microelectronics
US20080171647A1 (en) * 2007-01-17 2008-07-17 Wei-Chang Lee Low temperature cofired ceramic materials
US20090142578A1 (en) 2007-11-15 2009-06-04 Rutgers, The State University Of New Jersey Method of hydrothermal liquid phase sintering of ceramic materials and products derived therefrom
KR20110034747A (ko) * 2009-09-29 2011-04-06 (주)에스에이치이씨 고강도 저온소결 세라믹의 제조방법
KR20120136143A (ko) * 2011-06-08 2012-12-18 고려대학교 산학협력단 저온 소결용 압전체의 제조방법 및 이를 이용한 압전체

Family Cites Families (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4961778A (en) * 1988-01-13 1990-10-09 The Dow Chemical Company Densification of ceramic-metal composites
JP2588254B2 (ja) * 1988-07-30 1997-03-05 マツダ株式会社 耐摩性摺動部材
JP3863207B2 (ja) * 1994-09-28 2006-12-27 東燃ゼネラル石油株式会社 ランタンクロマイト系セラミックス、それを含有するセパレータ及び該セパレータを用いた固体電解質型燃料電池
JP3656129B2 (ja) * 1995-04-20 2005-06-08 秀明 高橋 炭酸カルシウム固化体の製造方法並びに製造用原料粉末及び原料粉末の製造方法
JP3315887B2 (ja) * 1997-01-28 2002-08-19 品川白煉瓦株式会社 炭素含有耐火物の製造方法
JP2005306725A (ja) * 2004-03-22 2005-11-04 Atsushi Nakahira ゼオライト成形体およびその製造方法
US20070102672A1 (en) * 2004-12-06 2007-05-10 Hamilton Judd D Ceramic radiation shielding material and method of preparation
CN101664979B (zh) * 2009-10-09 2011-09-28 山东双连制动材料有限公司 一种摩擦材料的制备方法
EP2608217B1 (en) * 2011-12-21 2014-07-16 Agfa-Gevaert A dispersion comprising metallic, metal oxide or metal precursor nanoparticles, a polymeric dispersant and a sintering additive
CN103848627A (zh) * 2012-11-28 2014-06-11 大连大友高技术陶瓷有限公司 一种氮化硅陶瓷
US10315357B2 (en) * 2013-11-06 2019-06-11 Rutgers, The State University Of New Jersey Production of monolithic bodies from a porous matrix using low temperature solidification in an additive manufacturing process

Patent Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH038752A (ja) 1989-06-02 1991-01-16 Toyota Central Res & Dev Lab Inc 粘土鉱物焼結体およびその製造方法
JPH107411A (ja) 1996-06-20 1998-01-13 Nakamichi Yamazaki 含水物質の焼結方法、リン酸塩固化体、炭酸カルシウム固化体及びそれらの製造方法
US20040159390A1 (en) * 2001-10-01 2004-08-19 Heraeus Incorporated Methods for making and using self-constrained low temperature glass-ceramic unfired tape for microelectronics
JP2004115297A (ja) 2002-09-25 2004-04-15 Shiraishi Kogyo Kaisha Ltd ハイドロキシアパタイト多孔質燒結体の製造方法
US20080171647A1 (en) * 2007-01-17 2008-07-17 Wei-Chang Lee Low temperature cofired ceramic materials
US20090142578A1 (en) 2007-11-15 2009-06-04 Rutgers, The State University Of New Jersey Method of hydrothermal liquid phase sintering of ceramic materials and products derived therefrom
US8313802B2 (en) 2007-11-15 2012-11-20 Rutgers, The State University Of New Jersey Method of hydrothermal liquid phase sintering of ceramic materials and products derived therefrom
KR20110034747A (ko) * 2009-09-29 2011-04-06 (주)에스에이치이씨 고강도 저온소결 세라믹의 제조방법
KR20120136143A (ko) * 2011-06-08 2012-12-18 고려대학교 산학협력단 저온 소결용 압전체의 제조방법 및 이를 이용한 압전체

Non-Patent Citations (5)

* Cited by examiner, † Cited by third party
Title
HE ET AL.: "Low-Temperature Sintering Li Mo0 /Nio. Zno.sFe 0 Magneto-Dielectric Composites for High-Frequency Application", J. AM. CERAM. SOC., vol. 97, no. 8, 2014, pages 1 - 5
KAHARI ET AL., J. AM. CERAM. SOC., vol. 98, no. 3, 2015, pages 687 - 689
KAHARI, HANNA ET AL.: "Improvements and modifications to room-temperature fabrication method for dielectric Li2MoO4 ceramics", JOURNAL OF THE AMERICAN CERAMIC SOCIETY, vol. 98, no. 3, 22 January 2015 (2015-01-22), pages 687 - 689, XP055385073 *
See also references of EP3356310A4
ZHOU ET AL.: "Microwave Dielectric Ceramics in Li O-Bi O -MoO System with Ultra-Low Sintering Temperatures", J. AM. CERAM. SOC., vol. 93, no. 4, 2010, pages 1096 - 100

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WO2018007409A1 (en) 2016-07-05 2018-01-11 ETH Zürich High performance ceramics from cold sintered nanoscale powders
WO2018039620A1 (en) * 2016-08-26 2018-03-01 Sabic-Gapt Method of making a ceramic composite material by cold sintering
WO2018039634A1 (en) * 2016-08-26 2018-03-01 Sabic-Gapt Ceramic-polymer composites obtained by a cold sintering process
CN111417611A (zh) * 2016-08-26 2020-07-14 沙特基础工业全球技术有限公司 通过冷烧结制备陶瓷复合材料的方法
JP2020532144A (ja) * 2017-08-25 2020-11-05 サビック グローバル テクノロジーズ ビー．ブイ． ポリマーおよびセラミックの冷間焼結材料を含む基板
US20220226895A1 (en) * 2019-09-30 2022-07-21 The Penn State Research Foundation Cold sintering process for densification and sintering of powdered metals
US12318841B2 (en) * 2019-09-30 2025-06-03 The Penn State Research Foundation Cold sintering process for densification and sintering of powdered metals
US20220363604A1 (en) * 2019-10-04 2022-11-17 The Penn State Research Foundation Hydroflux-assisted densification
GB2606204A (en) 2021-04-29 2022-11-02 Ilika Tech Ltd Component for use in an energy storage device or an energy conversion device and method for the manufacture thereof
WO2022229666A1 (en) 2021-04-29 2022-11-03 Ilika Technologies Ltd Component for use in an energy storage device or an energy conversion device and method for the manufacture thereof
CN115432998A (zh) * 2021-06-03 2022-12-06 中国科学院上海硅酸盐研究所 一种直书写用透明陶瓷浆料的制备方法
CN117383931A (zh) * 2023-10-12 2024-01-12 中国工程物理研究院材料研究所 一种冷烧结-闪烧技术的两联法细晶陶瓷制备方法

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