WO2011007001A2 - Verfahren zur herstellung poröser, siliziumbasierter werkstoffe und daraus abgeleiteter keramik-keramik und keramik-metall-verbundwerkstoffe und deren anwendungen - Google Patents
Verfahren zur herstellung poröser, siliziumbasierter werkstoffe und daraus abgeleiteter keramik-keramik und keramik-metall-verbundwerkstoffe und deren anwendungen Download PDFInfo
- Publication number
- WO2011007001A2 WO2011007001A2 PCT/EP2010/060349 EP2010060349W WO2011007001A2 WO 2011007001 A2 WO2011007001 A2 WO 2011007001A2 EP 2010060349 W EP2010060349 W EP 2010060349W WO 2011007001 A2 WO2011007001 A2 WO 2011007001A2
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- pyridine
- silicon
- adducts
- materials
- ceramic
- Prior art date
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B38/00—Porous mortars, concrete, artificial stone or ceramic ware; Preparation thereof
- C04B38/0022—Porous mortars, concrete, artificial stone or ceramic ware; Preparation thereof obtained by a chemical conversion or reaction other than those relating to the setting or hardening of cement-like material or to the formation of a sol or a gel, e.g. by carbonising or pyrolysing preformed cellular materials based on polymers, organo-metallic or organo-silicon precursors
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
- B01J—CHEMICAL OR PHYSICAL PROCESSES, e.g. CATALYSIS OR COLLOID CHEMISTRY; THEIR RELEVANT APPARATUS
- B01J20/00—Solid sorbent compositions or filter aid compositions; Sorbents for chromatography; Processes for preparing, regenerating or reactivating thereof
- B01J20/22—Solid sorbent compositions or filter aid compositions; Sorbents for chromatography; Processes for preparing, regenerating or reactivating thereof comprising organic material
- B01J20/26—Synthetic macromolecular compounds
- B01J20/262—Synthetic macromolecular compounds obtained otherwise than by reactions only involving carbon to carbon unsaturated bonds, e.g. obtained by polycondensation
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
- C01B21/00—Nitrogen; Compounds thereof
- C01B21/06—Binary compounds of nitrogen with metals, with silicon, or with boron, or with carbon, i.e. nitrides; Compounds of nitrogen with more than one metal, silicon or boron
- C01B21/068—Binary compounds of nitrogen with metals, with silicon, or with boron, or with carbon, i.e. nitrides; Compounds of nitrogen with more than one metal, silicon or boron with silicon
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
- C01B21/00—Nitrogen; Compounds thereof
- C01B21/082—Compounds containing nitrogen and non-metals and optionally metals
- C01B21/0821—Oxynitrides of metals, boron or silicon
- C01B21/0823—Silicon oxynitrides
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
- C04B35/58—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides
- C04B35/584—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on silicon nitride
- C04B35/589—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on silicon nitride obtained from Si-containing polymer precursors or organosilicon monomers
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
- C04B35/58—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides
- C04B35/597—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on silicon oxynitride, e.g. SIALONS
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/62227—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products obtaining fibres
- C04B35/62272—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products obtaining fibres based on non-oxide ceramics
- C04B35/62286—Fibres based on nitrides
- C04B35/62295—Fibres based on nitrides based on silicon nitride
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/626—Preparing or treating the powders individually or as batches ; preparing or treating macroscopic reinforcing agents for ceramic products, e.g. fibres; mechanical aspects section B
- C04B35/628—Coating the powders or the macroscopic reinforcing agents
- C04B35/62844—Coating fibres
- C04B35/62857—Coating fibres with non-oxide ceramics
- C04B35/62865—Nitrides
- C04B35/62871—Silicon nitride
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/626—Preparing or treating the powders individually or as batches ; preparing or treating macroscopic reinforcing agents for ceramic products, e.g. fibres; mechanical aspects section B
- C04B35/628—Coating the powders or the macroscopic reinforcing agents
- C04B35/62884—Coating the powders or the macroscopic reinforcing agents by gas phase techniques
-
- C—CHEMISTRY; METALLURGY
- C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
- C08G—MACROMOLECULAR COMPOUNDS OBTAINED OTHERWISE THAN BY REACTIONS ONLY INVOLVING UNSATURATED CARBON-TO-CARBON BONDS
- C08G77/00—Macromolecular compounds obtained by reactions forming a linkage containing silicon with or without sulfur, nitrogen, oxygen or carbon in the main chain of the macromolecule
- C08G77/04—Polysiloxanes
- C08G77/38—Polysiloxanes modified by chemical after-treatment
- C08G77/382—Polysiloxanes modified by chemical after-treatment containing atoms other than carbon, hydrogen, oxygen or silicon
- C08G77/388—Polysiloxanes modified by chemical after-treatment containing atoms other than carbon, hydrogen, oxygen or silicon containing nitrogen
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2002/00—Crystal-structural characteristics
- C01P2002/80—Crystal-structural characteristics defined by measured data other than those specified in group C01P2002/70
- C01P2002/82—Crystal-structural characteristics defined by measured data other than those specified in group C01P2002/70 by IR- or Raman-data
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2002/00—Crystal-structural characteristics
- C01P2002/80—Crystal-structural characteristics defined by measured data other than those specified in group C01P2002/70
- C01P2002/86—Crystal-structural characteristics defined by measured data other than those specified in group C01P2002/70 by NMR- or ESR-data
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2004/00—Particle morphology
- C01P2004/01—Particle morphology depicted by an image
- C01P2004/03—Particle morphology depicted by an image obtained by SEM
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2004/00—Particle morphology
- C01P2004/30—Particle morphology extending in three dimensions
- C01P2004/45—Aggregated particles or particles with an intergrown morphology
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2006/00—Physical properties of inorganic compounds
- C01P2006/10—Solid density
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2111/00—Mortars, concrete or artificial stone or mixtures to prepare them, characterised by specific function, property or use
- C04B2111/00474—Uses not provided for elsewhere in C04B2111/00
- C04B2111/00793—Uses not provided for elsewhere in C04B2111/00 as filters or diaphragms
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2111/00—Mortars, concrete or artificial stone or mixtures to prepare them, characterised by specific function, property or use
- C04B2111/20—Resistance against chemical, physical or biological attack
- C04B2111/28—Fire resistance, i.e. materials resistant to accidental fires or high temperatures
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/38—Non-oxide ceramic constituents or additives
- C04B2235/3817—Carbides
- C04B2235/3826—Silicon carbides
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/48—Organic compounds becoming part of a ceramic after heat treatment, e.g. carbonising phenol resins
- C04B2235/483—Si-containing organic compounds, e.g. silicone resins, (poly)silanes, (poly)siloxanes or (poly)silazanes
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/50—Constituents or additives of the starting mixture chosen for their shape or used because of their shape or their physical appearance
- C04B2235/52—Constituents or additives characterised by their shapes
- C04B2235/5208—Fibers
- C04B2235/5216—Inorganic
- C04B2235/522—Oxidic
- C04B2235/5224—Alumina or aluminates
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/50—Constituents or additives of the starting mixture chosen for their shape or used because of their shape or their physical appearance
- C04B2235/52—Constituents or additives characterised by their shapes
- C04B2235/5208—Fibers
- C04B2235/5264—Fibers characterised by the diameter of the fibers
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/60—Aspects relating to the preparation, properties or mechanical treatment of green bodies or pre-forms
- C04B2235/616—Liquid infiltration of green bodies or pre-forms
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/80—Phases present in the sintered or melt-cast ceramic products other than the main phase
-
- C—CHEMISTRY; METALLURGY
- C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
- C08G—MACROMOLECULAR COMPOUNDS OBTAINED OTHERWISE THAN BY REACTIONS ONLY INVOLVING UNSATURATED CARBON-TO-CARBON BONDS
- C08G77/00—Macromolecular compounds obtained by reactions forming a linkage containing silicon with or without sulfur, nitrogen, oxygen or carbon in the main chain of the macromolecule
- C08G77/04—Polysiloxanes
- C08G77/12—Polysiloxanes containing silicon bound to hydrogen
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
Definitions
- the invention relates to methods for producing porous, silicon-based materials and ceramic ceramics and ceramic-metal composites derived therefrom and their applications.
- the present invention relates to methods with which 3-dimensionally extended, network-like structures with 10 to 5,000 nm mesh size can be produced and their applications.
- the basic substance of these networks has a fibrous or ribbon-like morphology and consists of silicon-based polymers, namely polysilanes, polysiloxanes or polysilsesquioxanes or their copolymers, polysilazanes or polysilsesquiazanes or their copolymers, polysiloxazanes or polysilsesquioxazanes or their copolymers, polysilathians or polysilsesquithians or their copolymers, the solid state materials are selected from the group consisting of silicon, silicon oxides, silicon oxynitrides, silicon nitrides and / or silicon sulfides.
- Silicon is of interest, for example, in nanoporous form and in the form of nanotubes and nanowires as the anode material for lithium ion batteries with a very high specific storage density and as a potential sensor material.
- the nanostructured Si is prepared by a process in which suspensions of butyl-terminated silicon nanoparticles are first prepared by reduction of SiCU with sodium naphthalid and be produced using butyl lithium (BuLi) and then be infiltrated into nanoporous or nanoparticulate template of Al 2 O 3 or SiO 2 . To compensate for the volume loss by the evaporating solvent, the infiltration process z. T. be repeated several times. The Si nanoparticles are then consolidated in a high temperature process in the range of 900-1000 0 C with decomposition of the ligand shell. Free-standing or porous Si nanostructures can only be produced by a further process step, in which the template material is removed by means of a suitable etchant, such as hydrofluoric acid or aqueous NaOH solution.
- a suitable etchant such as hydrofluoric acid or aqueous NaOH solution.
- the method thus has the disadvantage that it comprises a plurality of process steps and z. T. costly or toxic agents such as elemental sodium, BuLi and hydrofluoric acid find use in it.
- Silicon nanowires are produced, for example, by etching processes of silicon substrates (WO 2008045301, WO 2009128800), electrochemical deposition processes in nanoporous membranes (FR 2934612) or deposition from the gas phase at high temperatures involving previously generated Si, SiO or SiS species from the gas phase (US 6313015) applied.
- oligo- and polysilanes are often synthesized by a reductive coupling of diorganodichlorosilanes with finely suspended sodium in an inert solvent.
- the production takes place according to the following equation 1:
- WO 2009143823 A2 describes a process for the preparation of polysilanes by reaction of SiCl 4 and H 2 in a microwave reactor. This process initially produces halogenated polysilanes, which are hydrogenated in a further process step.
- JP 2009221294 discloses a silicon-based nanostructured material having uniform pores of several nanometers in size and having good thermal resistance.
- the process for its preparation is based on the microphase separation of block copolymers, of which a polymer component is more thermally stable and contains silicon.
- the other polymer component is removed by a thermal treatment.
- No. 4,840,778 describes a process for preparing inorganic polysilazanes by reacting halosilane base adducts such as H 2 SiCl 2 .2Py with ammonia.
- halosilane base adducts such as H 2 SiCl 2 .2Py
- the reaction is carried out in solution or a large excess of pyridine at 0 0 C and the adduct formed subsequently treated with NH 3 .
- the resulting solid is dissolved in an organic solvent after the reaction to separate the by-product (ammonium chloride).
- the product obtained is a glassy solid and therefore has no structural similarity with the network-like structure of the invention.
- the object of the invention is, first, to develop a uniform and only a few steps process path, with which silicon-based, finely porous and one-, two- and three-dimensional nanostructured materials of different classes can be produced.
- the object is achieved by a process for producing porous materials from silicon-based polymers or silicon-based inorganic solid-state materials in which hydridochlorosilanes are reacted with pyridine or pyridine derivatives to give the corresponding hydridochlorosilane-pyridine or hydrido-chlorosilane-pyridine derivative adducts and these adducts are thermally decomposed ,
- hydrido-chlorosilane-pyridine or hydrido-chlorosilane-pyridine derivative adducts are first produced by reacting a hydridochlorosilane (H 3 SiCl, H 2 SiCl 2 and / or HSiCb) with pyridine or a pyridine derivative.
- 1 molar equivalent of the Hydridochlorosilans is reacted with 1, 75 to 10 molar equivalents of pyridine or a pyridine derivative.
- 1 molar equivalent of the hydridochlorosilane is reacted with 1.75 to 2.5 molar equivalents of pyridine or a pyridine derivative.
- Preferred embodiments of the nanofilament networks consist of oligo- or polysilanes, in particular hydriopolysilanes (HPS) and chlorohydridopolysilanes (CLHPS).
- HPS hydriopolysilanes
- CLHPS chlorohydridopolysilanes
- pyridine derivatives Particularly suitable as pyridine derivatives are derivatives which are unsubstituted at position 2 and / or 6 and therefore can co-ordinate particularly readily with the silicon in hydridochlorosilane.
- Preferred pyridine derivatives are especially 4-dimethylamino; 2- or 4-methyl; 2.4; 3,4- or 3,5-dimethyl; 4-ethyl; 4-tert-butyl; 4-vinyl or 3-bromopyridine.
- Dichlorosilane-pyridine adducts (Equation 2) are very reactive and decompose upon contact with minute traces of water.
- the dichlorosilane-pyridine adducts do not have a sharp melting point. This class of compounds has not been used for the preparation of oligo- and polysilanes.
- the Hydridochlorosilan pyridine adducts decompose when heated in two stages, the first stage in the temperature range of 85 0 C to 145 0 C of a mass loss of about 75% and the second in the temperature range of about 145 0 C to about 170 0 C is accompanied by a loss of mass of 12%.
- the decomposition is completed in this temperature range, the remaining solid having a mass of 13% based on the starting material is stable up to 300 ° C.
- the simultaneous investigation of the gas phase by IR spectroscopy confirms the formation of SiH species.
- Fig. 25 shows a Raman spectrum of the hydrogen-rich polysilane obtained in the thermal decomposition of a dichlorosilane-pyridine adduct.
- Fig. 26 shows a 29 Si-CP / MAS NMR spectrum of the polysilane after heating to about 200 ° C for 3 hours under vacuum.
- Table 1 29 Si-chemical shift of cyclosilane derivatives (Si n R 2 n) in ppm relative to TMS.
- T group The signal of ⁇ 2 ("T group") is due to a silicon atom substituted by three other silicon atoms, and the fourth substituent is a hydrogen atom.
- Fig. 27 shows a 29 Si CP / MAS NMR spectrum of the polysilane of HSiCl 3 * 2 Py
- the formation of the oligo- or polysilanes characterized as products most likely proceeds via a silylene mechanism. Similar results were found for polysilane formation by Cp 2 ZrCl 2 catalyzed poly-dehydrocoupling of PhSiH 3 .
- the stability of the hexacoordinate silicon adducts can be varied.
- the thermal stability of the starting compound increases.
- the synthesis of oligo- and polysilanes requires a higher temperature range for the more stable compounds.
- the composition of the material produced can be influenced.
- Scheme 1 Thermal decomposition of a dichlorosilane-pyridine adduct under vacuum.
- the parent compound pyridine is representative of all candidate pyridine-type bases, in particular the above-mentioned pyridine derivatives.
- reaction regime Due to the catalytic effect of the by-products towards an undesired dismutation of the silanes, an open reaction regime is involved o these are removed continuously from the reaction zone, a special meaning. This separation is preferably carried out by sublimation / distillation in vacuo.
- decomposition of the adducts (Scheme 1) is preferably carried out without solvent.
- the reaction temperatures are between 70 and 300 ° C., preferably between 170 and 300 ° C.
- topology and chemical composition of these nanofilament networks can be influenced by the choice of hydridochlorosilane, the base that coordinates it, the rate of heating, and the thermolysis atmosphere (vacuum, shielding gas, reactive gas).
- the mesh sizes or pore diameters in these networks are between about 10 to 5,000 nm, which is why, according to the recommendations of the IUPAC, they can be described as meso- or macroporous material.
- this crosslinking can preferably take place at defect sites, such as, for example, the surfaces, grain boundaries and gussets of the crystallites. This preforms a polygonal network.
- the decomposition reaction is accompanied by a small-scale local separation of the reaction products, network-type polysilane, pyridine and pyridine hydrochloride.
- the latter occupy a considerable volume fraction because of their molecular size and the stoichiometric ratios.
- thermally induced - and especially by the application of vacuum assisted - evaporation pore spaces are free and unwanted dismutation reactions, which go back to the catalytic effect of the pyridine derivative, suppressed.
- further assembly of the polysilane chains can take place by attractive forces and (subsequent covalent) cross-linking.
- Scheme 2 Idealized network polysilane formation process illustrated on a single crystallite of the starting material.
- R H, Cl, Py representative of all eligible pyridine-type bases, in particular the abovementioned pyridine derivatives.
- reactive gases such as water vapor, ammonia or hydrogen sulfide
- networks of polysiloxanes, polysilazanes, polysilathanes (Scheme 3, / n) and the corresponding polysilane copolymers (/ n) can therefore be prepared.
- the reactive gases can also be used in mixtures, with moist, d. H. not anhydrous ammonia gas as a favorable reagent for the production of polysiloxazane or polysilane-polysiloxazane copolymer occupies a preferred position.
- the addition of the reactive gases can either before the decomposition step at room temperature (RT) or slightly elevated temperature to 100 0 C (Scheme 3, reaction path (A)), during the decomposition step (temperature between 180 and 300 0 C), (Scheme 3, reaction path (B)) or a combination of (A) and (B), and in each case under atmospheric pressure or reduced pressure between 0.01 to 700 mbar.
- RT room temperature
- reaction path (A) reaction path between 180 and 300 0 C
- reaction path (B)) reaction path
- a combination of (A) and (B) and in each case under atmospheric pressure or reduced pressure between 0.01 to 700 mbar.
- Reaction path (A) usually leads to rigid, cage-like networks (see Example 11).
- the reactive gas diffuses preferentially along Kristaliitgrenzen and gussets of the polycrystalline Hydridochlorosilan- pyridine derivative adduct and leads here to a rigid cross-linking, so that the shape of the original grains is more fixed. Due to the higher initial crosslinking, higher yields are also obtained via this reaction path in comparison with the production of pure polysilane under reduced pressure or under protective gas.
- Reaction path (B) leads, in particular when lower partial pressures of the reactive gases are used, to more elastic, tissue-like networks, since in this case the network formation mechanism described above predominates with outgassing of pyridine and pyridine hydrochloride.
- All polymeric networks produced by one of the aforementioned methods can be pyrolyzed to silicon or to inorganic ceramics in a further or immediately subsequent process step at higher temperatures between 400 and 1200 ° C., preferably between 700 and 1100 ° C. It is a special feature of the method according to the invention that the network-like structure set by the aforementioned method steps, with their specific topological characteristics, is largely retained (see Examples 4 and 9).
- the chemical composition in turn, can be influenced by the starting material, the selected atmosphere, and the pyrolysis or aging temperature and duration (Scheme 4).
- Scheme 4 Preferred pyrolysis conditions and resulting elemental systems for the generation of nanofilament networks from silicon-based inorganic solid state materials.
- the specific surface termination depends again from the specific morphology of Ansgansmaterials, and the partial pressures of the reactive gases and temperatures during pyrolysis.
- the products produced by the process according to the invention are characterized in turn by novel morphological properties.
- the porous materials according to the invention have a network-like structure, consisting of filaments of silicon-based polymers or silicon-based inorganic solid-state materials, and are characterized in that the materials have an average mesh size between 10 and 5,000 nm, a mass density between 0.01 and 1, 5 g / cm 3 and have a silicon content of at least 20% by mass and the filaments are interconnected by nodes and branch points cohesively.
- the polymers consist of polysilanes, polysiloxanes or polysilsesquioxanes or their copolymers, polysilazanes or polysilsesquiazanes or their copolymers, polysiloxazanes or polysilsesquioxazanes or their copolymers, polysilathians or polysilsesquithians or copolymers thereof, the solid-state materials are selected from the group silicon, silicon oxides, silicon nitrides, silicon nitrides and / or silicon sulfides.
- the mass density of the materials according to the invention is 0.01 to 1.0 g / cm 3 .
- the mass density is preferably 0.01 to 0.5 g / cm 3 .
- the mass density is particularly preferably 0.01 to 0.3 g / cm 3 .
- the materials produced have a 3-dimensional, network-like, porous structure, a geometric mass density between 0.01 and 1.5 g / cm3, preferably below 0.3 g / cm3.
- the materials consist essentially of silicon-based polymers or silicon-based inorganic solid state materials, with a silicon content of at least 20 percent by mass.
- the polymers form rod-shaped or flat filaments, wherein the filaments are bonded together at intersections and branching points. These joints are made of the same material and are often thickened.
- connection partners ie the filaments
- connection partners ie the filaments
- the pores of the materials have a mesh size between 10 and 5,000 nm.
- the filaments have a length between 50 and 500 nm.
- the materials of the invention have versatile applications.
- the materials can serve as filter material because of their network-like structures.
- the invention further relates to the use of the materials as a separator, electrolyte or electrode material in lithium batteries, as a gas absorber and gas storage, for thermal insulation, for the modification and functionalization of surfaces, as a support material for catalysts and other active ingredients, as well as for the production of bicontinuous polymer Polymer, ceramic polymer, ceramic-ceramic and ceramic-metal composites.
- FIGS. 14-16 are electron micrographs of the thermolysis product of FIG.
- Fig. 22 is a false-color elemental distribution image of an aluminum-infiltrated mesoporous Si / O / N sample
- FIG. 23 shows an electron micrograph and a false-color elemental distribution image of the infiltration front of the Al metal in the Si / O / N-
- Fig. 24 is an electron micrograph of a bicontinuous
- Si / O / N-SiC ceramic-ceramic composite material Si / O / N-SiC ceramic-ceramic composite material.
- the hydridochlorosilane-pyridine (Py) adducts are prepared by initially charging 5 mmol of the hydridochlorosilane in 20 ml of toluene under isopropanol / dry ice cooling. To this solution is added slowly 10 mmol of the corresponding pyridine base. The suspension is slowly warmed to room temperature within one hour and then filtered off. The resulting white solid from the Hydridochlorosilan- pyridine adduct formed is dried under vacuum.
- Embodiment 3 Thermal decomposition of H 2 SiCl 2 * 2 (4-DMAP)
- Embodiment 4 Thermal decomposition of HSiCl 3 * 2 Py
- a small amount of the product is pressed under inert gas atmosphere on a commercial sample holder for scanning electron microscopy with self-adhesive carbon support film, then coated in a commercial plasma sputtering system with argon working gas with an approximately 5 nm thick, antistatic gold layer and examined in a high-resolution scanning electron microscope (Fig 1 - 3). Before sputtering and introduction into the microscope, the product is exposed to normal ambient air for a few minutes each time.
- a fleece-like, elastic material which consists of 20 to 70 nm thick nanofibers linked by common nodal points (FIG. 2).
- the mesh sizes of the network are predominantly between 50 and 650 nm and are distributed homogeneously over large areas of the material (FIG. 3).
- a semiquantitative analysis by means of EDX energy dispersive energy revealed an approximate element content of 34 at% Si and 52 at% oxygen, 7 at% carbon, and 2% chlorine (hydrogen ignored).
- polysilane / polysiloxane nanofilament network considerably incorporates oxygen. This can be done by hydrolysis or insertion of oxygen during the sample preparation, in particular during the above-mentioned, short-term handling in air, as well as by residual oxygen during sputtering in the argon plasma.
- the material can thus be used to remove oxygen or residual moisture from gases and media.
- the insertion product of polysilane with oxygen into the Si-Si bond is a polysiloxane.
- a small amount of the product is applied under a protective gas atmosphere to a commercially available sample holder for scanning electron microscopy with self-adhesive carbon carrier film and then examined in a high-resolution scanning electron microscope (FIGS. 4 to 6). Before being introduced into the microscope, the product is exposed for a few minutes to normal ambient air.
- thermolysis product shows a coarser and more irregular topology compared to that made from H 2 SiCl 2 * 2Py ( Figure 4).
- the webs of the network are often formed flat.
- the thickness of the cylindrical ridges varies between 20 and 80 nm.
- the meshes of the network are often elongated, with diameters of 200 to 1500 nm ( Figure 5).
- the material also contains 20 -4 0 micron, open pore spaces (Fig. 6).
- a Schlenk vessel is charged with 1.55 g (4.2 mmol) of dichlorosilane-4-tert-butylpyridine adduct.
- a small amount of the product is applied under a protective gas atmosphere to a commercially available sample holder for scanning electron microscopy with self-adhesive carbon carrier film and then examined in a high-resolution scanning electron microscope (FIGS. 7-10). Before being introduced into the microscope, the product is exposed to normal ambient air for a few minutes.
- a nonwoven, elastic material which consists of 15 to 40 nm thick nanofibers linked by common nodal points and parallel bundles (FIG. 8).
- the nanofiber fleece lies flat in 100-150 ⁇ m thick layers (FIGS. 7, 9) and is very dense, with effective mesh sizes of a few 10 nm (FIG. 10).
- a small amount of the product is pressed under a protective gas atmosphere onto a commercially available sample carrier for scanning electron microscopy with a self-adhesive carbon carrier film and subsequently examined in a high-resolution scanning electron microscope (FIGS. 11-13). Before being introduced into the microscope, the product is exposed to normal ambient air for a few minutes.
- a particulate, porous material has formed, which consists of 10 to about 70 micron large, spherical and fractal formations.
- the fine structure of these structures can be described as rigid and skeletal, with flat, consisting of a dense nanofiber network segments enclose several micron pores and are interrupted at the surface of these (Figure 12).
- the nanofibers have a nodular or nodular morphology and are linked predominantly via common nodal points and less via parallel bundles (FIG. 13).
- a small amount of the product is placed under a protective gas atmosphere on a commercially available sample holder for scanning electron microscopy with self-adhesive carbon carrier film and then examined in a high-resolution scanning electron microscope (FIGS. 14-17). Before being introduced into the microscope, the product is exposed to normal ambient air for a few minutes.
- FIGS. 14 and 15 it can be seen that a particulate, porous material has formed, which consists of 0.5 to approximately 3 ⁇ m large, spherical and / or fractal structures. These are the former crystallites of the H 2 SiCl 2 * 2 Py adduct.
- the fine structure of these particles can be described as rigid and skeletal, with their inner, in contrast to Example 4 is not largely hollow.
- the particles are partially interconnected by 20 to 100 nm thick fibrils (Figure 16).
- Figure 16 In the high resolution (Fig. 17) it can be seen that the particles are constructed as opposed to the out of H 2 SiCl 2 * 2 Py and H 2 SiCl 2 * 2 thermolysis tBuPy prepared with fibrillar polysilane predominantly of sheet or platy polysilane.
- Embodiment 10 Fabrication of a mesoporous Si / O / N network
- Example 4 A small amount of the product of Example 4 is placed under a protective gas atmosphere in a quartz glass boat and then in a quartz glass Schlenk tube (diameter: 40 mm) in a gas stream of nitrogen and anhydrous ammonia pyrolyzed.
- the heating program and the gas flows are as follows:
- a sample of the material was placed under a protective gas atmosphere on a commercially available sample holder for scanning electron microscopy with self-adhesive carbon carrier film and then examined in a high-resolution scanning electron microscope.
- a product obtained in this way could e.g. B. serve as a support material for Si / N-based catalysts.
- Embodiment 11 Preparation of a mesoporous Si / O / N-network by direct ammonolysis of H 2 SiCl 2 * 2Py
- a density of 0.3 g / cm 3 was measured.
- a sample of the substance was placed under a protective gas atmosphere on a commercially available sample holder for scanning electron microscopy with self-adhesive carbon carrier film and then examined in a high-resolution scanning electron microscope.
- the material consists of a porous, cellular network with ridges of several tens to several hundreds of nm, with the individual cells or cages representing the size and shape of the original H 2 SiCl 2 ZPy crystallites.
- a tube of porous alumina ceramic (diameter: 10 mm, wall thickness: 1 mm, particle size 1-5 microns) is dried for 8 hours at 140 0 C, and then transferred into a SchutzgasJes quartz glass tube.
- Quartz glass tube are then via a cannula in inert gas countercurrent
- Atmospheric pressure subjected to the following heating and gassing scheme:
- the Al 2 O 3 tube is broken to examine the concave inner surface. A fragment was pressed onto a commercially available sample holder for scanning electron microscopy with self-adhesive carbon carrier film and then examined in a high-resolution scanning electron microscope. The handling after the high-temperature ammonolysis was carried out in air.
- Fig. 19 shows a section of the inner surface of the porous Al 2 O 3 ceramic.
- the 1 to 5 ⁇ m corundum grains are covered by a fine Si / O / N network, which has also grown into the intervening pores.
- the effective pore size is reduced and the composite material thus prepared is to be used as a microfilter.
- Small burner tests on the above-mentioned free Si / O / N material, which resulted from the excess pyridine in the quartz glass tube, showed that it can be heated to red-hot without changing its shape.
- the filter material is also dimensionally stable and temperature-resistant in air.
- organic contaminants retained by a filter material made by the process presented can be removed by burning out the filter and the filter material so regenerated.
- Embodiment 13 Hydrophilic and superhydrophobic mesoporous Si / O / N and SiO 2 networks
- HMDS hexamethyldisilazane
- a method for producing anti-fogging layers of SiO 2 and SiO 2 / TiO 2 nanofibers by flame spray pyrolysis Furthermore, the materials produced by the process are suitable for the phase separation of hydrophilic and hydrophobic liquids.
- a mesoporous silica-SiO 2 material prepared by the method proposed in Example 9 is also suitable for these purposes.
- Embodiment 14 Preparation of bicontinuous aluminum Si / O / N
- a material sample (about 1 ⁇ 2 ⁇ 0.5 mm) of the mesoporous Si / O / N prepared according to embodiment 7 is evacuated in a vacuum recipient with a thermal evaporator unit to 1 ⁇ 10 -3 mbar residual gas pressure (N 2 or Ar) and vaporized thermally with aluminum by means of an electrically heated tungsten filament.
- the distance to the incandescent filament is 5 millimeters, the dimensions of the inserted into the coil Al-plate are 2 x 1 x 0.015 mm.
- the filament glows bright yellow to white and the evaporation is continued until all the aluminum has evaporated.
- the initially pure white sample then appears light to dark gray.
- the vapor deposition is necessary to provide wettability of the Si / O / N with molten metals.
- an infiltration with aluminum hydride AIH 3 in ethyl ether with its downstream, thermal decomposition take place.
- a (partial) infiltration is carried out with molten aluminum.
- an approximately 0.1 mm thick plate of hexagonal boron nitride is placed on the incandescent filament and successively placed another aluminum plate (about 2 x 1 x 0.3 mm) and the previously vapor-deposited sample in the direction of their vapor-deposited surface.
- the infiltration is preferably carried out in vacuo at 1 * 10 ⁇ 3 mbar or under argon. Nitrogen is to be avoided in this process step as a protective gas or in the residual gas, since otherwise forms a infiltration obstructing nitride layer on the molten metal.
- the evaporation recipient is evacuated and purged several times with argon. The heating power of the incandescent filament is increased until the melting of the aluminum plate and then left constant for a few minutes.
- the sample is silvery-gray after this treatment. It was pressed onto a commercially available sample holder for scanning electron microscopy with self-adhesive carbon carrier film and then examined in a high-resolution scanning electron microscope.
- Fig. 22 visualizes the (partial) infiltration of the Si / O / N sample with aluminum by a false color elemental distribution image produced by the EDX method.
- Fig. 23 such a false color element distribution image is contrasted with the infiltration front of a scanning electron micrograph. It can be clearly deduced from the surface morphology of the Al-containing sample part, ZO that the aluminum has penetrated into the pore spaces of the mesoporous Si / O / N network. Since the Si / O / N in this network is already present as a continuous phase and it has exclusively, or in large part, an open porosity, a bicontinuous ceramic-metal composite is present in the AI-infiltrated area. This fact will become more apparent from the partial infiltrations of aluminum shown in Fig. 24 into the surface of the mesoporous Si / O / N network.
- Embodiment 15 Preparation of a bicontinuous ceramic-polymer composite material, and a bicontinuous Si / O / N-SiC ceramic-ceramic composite material
- the polymer is then crosslinked and pyrolyzed by means of the thermal evaporator unit already presented in Example 10 above.
- an approximately 0.1 mm thick plate of hexagonal boron nitride is placed on the filament and then placed on the infiltrated sample.
- the infiltration is preferably carried out under atmospheric pressure or elevated pressure in order to keep the outgassing of low molecular weight fragments low and to achieve a high ceramic yield.
- the heating power of the filament is slowly increased to its bright white heat.
- the boron nitride plate and the area of the sample facing the heat source glow bright or dark red. After switching off the heating, the heated sample side is colored black by the pyrolysis of the polymer. It turns out, however, that the polymer on the side facing away from the heat source even after prolonged heating still has a light color and therefore was not pyrolyzed. This is due to the poor thermal conductivity and thus to the good thermal insulation properties of the mesoporous Si / O / N network.
- the sample was applied to a commercially available sample holder for scanning electron microscopy with self-adhesive carbon carrier film and then examined in a high-resolution scanning electron microscope. Infiltration with the preceramic polymer and its pyrolysis resulted in a bicontinuous Si / O / N-SiC ceramic-ceramic composite material.
- FIG. 24 shows an interface between the still unfiltered Si / O / N network and the composite material produced in the upper image area.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Organic Chemistry (AREA)
- Ceramic Engineering (AREA)
- Manufacturing & Machinery (AREA)
- Materials Engineering (AREA)
- Structural Engineering (AREA)
- Inorganic Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Analytical Chemistry (AREA)
- General Chemical & Material Sciences (AREA)
- Health & Medical Sciences (AREA)
- Medicinal Chemistry (AREA)
- Polymers & Plastics (AREA)
- Nanotechnology (AREA)
- Dispersion Chemistry (AREA)
- Silicon Polymers (AREA)
Abstract
Description
Claims
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE112010002933.4T DE112010002933A5 (de) | 2009-07-16 | 2010-07-16 | Verfahren zur Herstellung poröser, siliziumbasierter Werkstoffe und daraus abgeleiteter Werkstoffe und deren Anwendungen |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE102009033351.7 | 2009-07-16 | ||
DE200910033351 DE102009033351B3 (de) | 2009-07-16 | 2009-07-16 | Verfahren zur Herstellung von Oligo- und Polysilanen |
Publications (2)
Publication Number | Publication Date |
---|---|
WO2011007001A2 true WO2011007001A2 (de) | 2011-01-20 |
WO2011007001A3 WO2011007001A3 (de) | 2011-03-17 |
Family
ID=43416514
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/EP2010/060349 WO2011007001A2 (de) | 2009-07-16 | 2010-07-16 | Verfahren zur herstellung poröser, siliziumbasierter werkstoffe und daraus abgeleiteter keramik-keramik und keramik-metall-verbundwerkstoffe und deren anwendungen |
Country Status (2)
Country | Link |
---|---|
DE (2) | DE102009033351B3 (de) |
WO (1) | WO2011007001A2 (de) |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE102014012198A1 (de) | 2014-08-16 | 2016-02-18 | Technische Universität Bergakademie Freiberg | Wasserstoffhaltige Polysilathiane, Verfahren zu deren Herstellung und deren Verwendung |
WO2016156384A1 (de) * | 2015-03-31 | 2016-10-06 | Universität Paderborn | Verfahren zum herstellen eines nano- oder mikrostrukturierten schaumstoffs |
DE102016116732A1 (de) | 2016-09-07 | 2018-03-08 | Technische Universität Darmstadt | Verfahren zum Herstellen poröser Keramiken und eines porösen Keramikprodukts |
Families Citing this family (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE102019102842B4 (de) | 2019-02-05 | 2024-02-08 | Karl Schickinger | Verfahren zur Herstellung von Organohydrogenpolysiloxanen |
Citations (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4840778A (en) | 1983-12-29 | 1989-06-20 | Toa Nenryo Kogyo Kabushiki Kaisha | Inorganic polysilazane and method of producing the same |
US6313015B1 (en) | 1999-06-08 | 2001-11-06 | City University Of Hong Kong | Growth method for silicon nanowires and nanoparticle chains from silicon monoxide |
WO2008045301A1 (en) | 2006-10-05 | 2008-04-17 | Hitachi Chemical Co., Ltd. | Well-aligned, high aspect-ratio, high-density silicon nanowires and methods of making the same |
JP2009221294A (ja) | 2008-03-14 | 2009-10-01 | Ricoh Co Ltd | ナノ構造材料とその作製方法 |
WO2009128800A1 (en) | 2008-04-17 | 2009-10-22 | The Board Of Trustees Of The University Of Illinois | Silicon nanowire and composite formation and highly pure and uniform length silicon nanowires |
WO2009143823A2 (de) | 2008-05-27 | 2009-12-03 | Rev Renewable Energy Ventures, Inc. | Halogeniertes polysilan und plasmachemisches verfahren zu dessen herstellung |
FR2934612A1 (fr) | 2008-07-30 | 2010-02-05 | Univ Reims Champagne Ardenne | Dispositif d'elaboration a temperature ambiante de nanofils de si par electrodeposition, procede de preparation et nanofils obtenus |
Family Cites Families (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0781815B1 (de) * | 1995-07-13 | 2010-11-17 | AZ Electronic Materials USA Corp. | Zusammensetzung und verfahren zur herstellung von keramischen materialien |
DE102004058119A1 (de) * | 2004-12-02 | 2006-06-08 | Daimlerchrysler Ag | Poröse SiC-Körper mit Mikrokanälen und Verfahren zu deren Herstellung |
-
2009
- 2009-07-16 DE DE200910033351 patent/DE102009033351B3/de not_active Expired - Fee Related
-
2010
- 2010-07-16 DE DE112010002933.4T patent/DE112010002933A5/de not_active Withdrawn
- 2010-07-16 WO PCT/EP2010/060349 patent/WO2011007001A2/de active Application Filing
Patent Citations (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4840778A (en) | 1983-12-29 | 1989-06-20 | Toa Nenryo Kogyo Kabushiki Kaisha | Inorganic polysilazane and method of producing the same |
US6313015B1 (en) | 1999-06-08 | 2001-11-06 | City University Of Hong Kong | Growth method for silicon nanowires and nanoparticle chains from silicon monoxide |
WO2008045301A1 (en) | 2006-10-05 | 2008-04-17 | Hitachi Chemical Co., Ltd. | Well-aligned, high aspect-ratio, high-density silicon nanowires and methods of making the same |
JP2009221294A (ja) | 2008-03-14 | 2009-10-01 | Ricoh Co Ltd | ナノ構造材料とその作製方法 |
WO2009128800A1 (en) | 2008-04-17 | 2009-10-22 | The Board Of Trustees Of The University Of Illinois | Silicon nanowire and composite formation and highly pure and uniform length silicon nanowires |
WO2009143823A2 (de) | 2008-05-27 | 2009-12-03 | Rev Renewable Energy Ventures, Inc. | Halogeniertes polysilan und plasmachemisches verfahren zu dessen herstellung |
FR2934612A1 (fr) | 2008-07-30 | 2010-02-05 | Univ Reims Champagne Ardenne | Dispositif d'elaboration a temperature ambiante de nanofils de si par electrodeposition, procede de preparation et nanofils obtenus |
Non-Patent Citations (2)
Title |
---|
KIM, H.; HAN, B.; CHOO, J.; CHO, J.: "Three-Dimensional Porous Silicon Particles for Use in High-Performance Lithium Secondary Batteries", ANGEWANDTE CHEMIE-INTERNATIONAL EDITION, vol. 47, 2008, pages 10151 - 10154, XP002739635, DOI: doi:10.1002/anie.200804355 |
PARK, M.-H.; KIM, M. G.; JOO, J.; KIM, K.; KIM, J.; AHN, S.; CUI, Y.; CHO J., SILICON NANOTUBE BATTERY ANODES NANO LETTERS, vol. 9, 2009, pages 3844 - 3847 |
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE102014012198A1 (de) | 2014-08-16 | 2016-02-18 | Technische Universität Bergakademie Freiberg | Wasserstoffhaltige Polysilathiane, Verfahren zu deren Herstellung und deren Verwendung |
DE102014012198B4 (de) * | 2014-08-16 | 2016-03-10 | Technische Universität Bergakademie Freiberg | Wasserstoffhaltige Polysilathiane, Verfahren zu deren Herstellung und deren Verwendung |
WO2016156384A1 (de) * | 2015-03-31 | 2016-10-06 | Universität Paderborn | Verfahren zum herstellen eines nano- oder mikrostrukturierten schaumstoffs |
DE102016116732A1 (de) | 2016-09-07 | 2018-03-08 | Technische Universität Darmstadt | Verfahren zum Herstellen poröser Keramiken und eines porösen Keramikprodukts |
Also Published As
Publication number | Publication date |
---|---|
WO2011007001A3 (de) | 2011-03-17 |
DE112010002933A5 (de) | 2014-08-07 |
DE102009033351B3 (de) | 2011-02-24 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
KR102301706B1 (ko) | 맥신 섬유의 제조방법 및 이로부터 제조된 맥신 섬유 | |
Caruso et al. | Titanium dioxide tubes from sol–gel coating of electrospun polymer fibers | |
EP1200653B1 (de) | Meso- und nanoröhren | |
EP1969166B1 (de) | Nano-thermoelektrika | |
KR101407236B1 (ko) | 그래핀 함유 흑연나노섬유 및 그 제조방법, 이를 포함하는 리튬이차전지의 전극물질 | |
DE102014211012A1 (de) | Herstellungsverfahren für einen Silicium-Kohlenstoff-Komposit | |
EP3423403B1 (de) | Verfahren zur herstellung eines silicium-kohlenstoff-komposites | |
JP2020528876A (ja) | 小分子系自立フィルムおよびハイブリッド材料 | |
US20150139888A1 (en) | Titanium carbide (tic) nano-fibrous felts | |
WO2011007001A2 (de) | Verfahren zur herstellung poröser, siliziumbasierter werkstoffe und daraus abgeleiteter keramik-keramik und keramik-metall-verbundwerkstoffe und deren anwendungen | |
KR102085940B1 (ko) | 다중벽 탄소나노튜브의 대량 생산을 위한 촉매 | |
Zhu et al. | Direct fabrication of single-walled carbon nanotube macro-films on flexible substrates | |
DE202012011892U1 (de) | Kohlenstoffnanomaterial | |
Cheung et al. | Conversion of bamboo to biomorphic composites containing silica and silicon carbide nanowires | |
CN108699684A (zh) | 化学气相沉积法构建三维泡沫状结构 | |
WO2012093776A2 (ko) | 무기-나노구조체 복합소재 제조방법, 이를 이용한 탄소나노튜브 복합체 제조 방법 및 이에 의하여 제조된 탄소나노튜브 복합체 | |
US20110171096A1 (en) | High Throughput Synthesis of Carbide Nanostructures from Natural Biological Materials | |
EP0659806B1 (de) | Präkeramische Polyborosilazane, Verfahren zu deren Herstellung sowie daraus erhältliches keramisches Material | |
WO2019091506A1 (de) | Verfahren zur herstellung von hydrogenierten amorphen siliciumhaltigen kolloiden und/oder komposit-kolloiden und zur verkapselung von substanzen mit hydrogenierten amorphen siliciumhaltigen komposit-kolloiden, sowie hydrogenierte amorphe siliciumhaltige kolloide und/oder komposit-kolloide und mit siliciumhaltigen komposit-schichten verkapselte substanzen und deren verwendung | |
KR20220098208A (ko) | 나노와이어 네트워크 | |
Wang et al. | Macroporous SiC MoSi2 ceramics from templated hybrid MoCl5–polymethylsilane | |
DE102006006675A1 (de) | Antimikrobielle polymerabgeleitete Silber-(Kupfer)-Nanokomposite | |
WO2014082815A1 (de) | Verfahren zum herstellen kohlenstoffhaltiger hydridosilane | |
DE19503976C1 (de) | Herstellung einkristalliner dünner Schichten aus SiC | |
EP1786726A2 (de) | Mesoporöses boronnitrid mit einer homogenen und geordneten porosität und einer hochspezifischen oberfläche und herstellungsverfahren |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 10739311 Country of ref document: EP Kind code of ref document: A2 |
|
WWE | Wipo information: entry into national phase |
Ref document number: 112010002933 Country of ref document: DE Ref document number: 1120100029334 Country of ref document: DE |
|
122 | Ep: pct application non-entry in european phase |
Ref document number: 10739311 Country of ref document: EP Kind code of ref document: A2 |
|
NENP | Non-entry into the national phase |
Ref country code: DE Effective date: 20120117 |
|
REG | Reference to national code |
Ref country code: DE Ref legal event code: R225 Ref document number: 112010002933 Country of ref document: DE Effective date: 20140807 |