WO2013167306A1 - Bornitrid-agglomerate, verfahren zu deren herstellung und deren verwendung - Google Patents

Bornitrid-agglomerate, verfahren zu deren herstellung und deren verwendung Download PDF

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Publication number
WO2013167306A1
WO2013167306A1 PCT/EP2013/055724 EP2013055724W WO2013167306A1 WO 2013167306 A1 WO2013167306 A1 WO 2013167306A1 EP 2013055724 W EP2013055724 W EP 2013055724W WO 2013167306 A1 WO2013167306 A1 WO 2013167306A1
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WIPO (PCT)
Prior art keywords
boron nitride
agglomerates
binder phase
agglomerates according
aluminum
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/EP2013/055724
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German (de)
English (en)
French (fr)
Inventor
Martin Engler
Krishna Uibel
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.)
ESK Ceramics GmbH and Co KG
Original Assignee
ESK Ceramics GmbH and Co KG
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
Application filed by ESK Ceramics GmbH and Co KG filed Critical ESK Ceramics GmbH and Co KG
Priority to CN201380024435.3A priority Critical patent/CN104284860B/zh
Priority to BR112014028119A priority patent/BR112014028119A8/pt
Priority to US14/399,664 priority patent/US9371449B2/en
Priority to EP13713123.1A priority patent/EP2847129B1/de
Priority to KR1020147033982A priority patent/KR102079972B1/ko
Priority to JP2015510691A priority patent/JP6122101B2/ja
Publication of WO2013167306A1 publication Critical patent/WO2013167306A1/de
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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    • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
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    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08K—Use of inorganic or non-macromolecular organic substances as compounding ingredients
    • C08K3/00—Use of inorganic substances as compounding ingredients
    • C08K3/38—Boron-containing compounds
    • C08K2003/382—Boron-containing compounds and nitrogen
    • C08K2003/385—Binary compounds of nitrogen with boron
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
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    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/29—Coated or structually defined flake, particle, cell, strand, strand portion, rod, filament, macroscopic fiber or mass thereof
    • Y10T428/2982—Particulate matter [e.g., sphere, flake, etc.]

Definitions

  • the present invention relates to boron nitride agglomerates or agglomerates based on boron nitride comprising hexagonal boron nitride, a process for their preparation and the use of such agglomerates as fillers for polymers for the production of polymer-boron nitride composite materials.
  • Hexagonal boron nitride powder due to its good thermal conductivity, can be used as a filler for polymers in applications where a good electrical insulation capability of the filler used is required at the same time. Furthermore, boron trid- powder is also used as sinter powder for hot pressing for applications in metallurgy. In addition, hexagonal boron nitride powder is used in cosmetic preparations, as a lubricant, as a release agent in metallurgy and as a raw material for the production of cubic boron nitride. Hexagonal boron nitride powder is technically synthesized by nitriding boric acid in the presence of a nitrogen source.
  • Ammonia can be used as the nitrogen source, in which case calcium phosphate is usually used as support material for the boric acid.
  • an organic nitrogen source such as melamine or urea can be reacted under nitrogen with boric acid or borates.
  • the nitriding is usually carried out at temperatures of 800 to 1200 ° C.
  • the resulting boron nitride is largely amorphous, it is also referred to as turbostratic boron nitride. From the amorphous boron nitride, hexagonal crystalline boron nitride is preferably produced in a nitrogen atmosphere at higher temperatures up to about 2100 ° C.
  • hBN hexagonal boron nitride
  • Typical platelet sizes are in the range of about 1 to 20 ⁇ , but also platelet sizes up to 50 ⁇ and more are possible.
  • the annealed material is ground or deagglomerated after production in order to obtain workable powders.
  • the thermal conductivity of the hexagonal boron nitride is greater in the platelet plane (a-axis) than perpendicular to it (c-axis). In the direction of the c-axis the thermal conductivity is 2.0 W / mK, in the direction of the a-axis it is 400 W / mK (see RF Hill, SMTA National Symposium “Emerging Packaging Technologies", Research Triangle Park, NC, Nov. 18 -21, 1996).
  • hexagonal boride tride powder for filler formulations is also often used in the form of granules prepared in a targeted manner, ie. in the form of secondary particles composed of the primary particles.
  • the granulation improves the processing properties, such as the flowability and the meterability, of the boron nitride powder, and it is possible to achieve higher fill levels and higher thermal conductivities, for example in polymer boron nitride composites.
  • There are various methods for producing such secondary particles which lead to granules with different morphology and different properties.
  • agglomerates is often used for the purposefully produced granules, as well as for the agglomerates or aggregates resulting from the production process during the synthesis of the hexagonal boron nitride.
  • Known methods for producing granules are build-up granulation and spray granulation.
  • spray granulation a suspension of solid in a liquid is used, which is atomized into droplets and then applied to droplets. be dried.
  • build-up granulation a small amount of liquid is added to the solid, which agglomerates the solid primary particles due to surface wetting and capillary forces, these agglomerates are then dried.
  • secondary particles of low density or high porosity are obtained.
  • No. 2006/0 127 422 A1 describes a process for producing spherical boron nitride agglomerates in which platelet-shaped hexagonal boron nitride is spray-dried from an aqueous suspension with an organic binder. The spray drying results in spherical boron nitride granules having an average agglomerate size of 1 to 500 ⁇ m. The spray granules are flowable in contrast to the starting powder.
  • WO 03/013 845 A1 describes a process for producing spherical boron nitride granules in which primary particles of hexagonal boron nitride are spray-dried with addition of polycarboxylic acids, silanes or organometallic compounds and the resulting spray granules are then sintered at temperatures between 1800 and 2400 ° C. become.
  • One possibility for producing boron nitride granules for filler applications is described in US Pat. No. 6,048,511 and EP 0 939 066 A1.
  • hexagonal boron nitride powder is processed into particles whose size distribution extends over a minimum size range of 100 ⁇ , the milled hBN powder is cold pressed, then granules are produced by breaking the cold-pressed molded body, and finally the so resulting granules sieved to obtain agglomerates of a desired size range.
  • breaking and cold pressing moldings can be pressed with a density of up to 1.91 g / cm 3 , from which granules are produced by breaking.
  • a disadvantage of this method is that it is very complicated, since first a special size distribution of the starting powder are set and then compacted and comminuted in several steps.
  • US 2004/0 208 812 A1 describes a process for producing a boron nitride powder containing boron nitride agglomerates, in which hexagonal boron nitride having an average platelet size of at least 2 ⁇ m is pressed into green bodies, and the green bodies are then pressed at temperatures above 1400 ° C sintered to densities of 1.4 to 1.7 g / cm 3 and then the resulting sintered bodies are ground.
  • WO 2005/021 428 Al a process for the preparation of boron nitride agglomerates low and medium density is described in which turbo stratisches or hexagonal boron nitride powder having a particle size of at most 5 ⁇ a temperature treatment above 1400 ° C, preferably 1850 to 1900 ° C, and then ground. Before the temperature treatment, the boron nitride powder can be isostatically pressed into shaped bodies and ground.
  • the resulting agglomerates are spherical to cube-shaped and the agglomerates have isotropic properties.
  • No. 5,854,155 and US Pat. No. 6,096,671 describe a process for the preparation of aggregated platelet-shaped boron nitride particles in which the boron nitride platelets in the aggregates without binder are bonded to one another.
  • the boron nitride aggregates are pine-cone-shaped, they are already formed in the synthesis of hexagonal boron nitride from boric acid, melamine and crystallization catalyst.
  • the thermal conductivity in the compound is reduced.
  • the surface of the filler increases in the disintegration of the agglomerates, so that the Theological properties of the compounds are deteriorated so much that the achievable filler content in the compound is reduced, which further deteriorates the achievable thermal conductivity.
  • the invention is therefore based on the object, overcoming the disadvantages of the prior art boron nitride agglomerates with good mechanical stability to provide, in particular for applications as a filler for polymers.
  • a further object of the invention is to provide a cost-effective, simple method for producing boron nitride agglomerates with good mechanical stability.
  • the above object is achieved by boron nitride agglomerates according to claim 1, a method for producing such boron nitride agglomerates according tonovalO and a polymer-boron nitride composite material according to claim 20.
  • the invention thus boron nitride agglomerates comprising hexagonal boron nitride primary particles, wherein the hexagonal boron nitride primary particles with each other by means an inorganic binder phase comprising at least one nitride and / or oxynitride are connected.
  • the invention also provides a process for producing such boron nitride agglomerates, wherein boron nitride starting powder in the form of boron nitride primary particles mixed with binder phase raw materials, processed into granules or moldings and this then a temperature treatment at a temperature of at least 1000 ° C in a Subjected to nitridieratmo sphere and
  • the resulting granules or shaped bodies are comminuted and / or fractionated.
  • the boron nitride agglomerates according to the invention can also be referred to as nitride-bonded boron nitride agglomerates or as boron nitride agglomerates with nitridic binder phase.
  • the invention furthermore relates to a polymer-boron nitride composite comprising boron nitride agglomerates according to the invention.
  • the agglomerates according to the invention are structured in their structure from many individual boron nitride platelets, which are connected to one another via a binder phase.
  • the binder phase comprises at least one nitride and / or oxynitride.
  • the boron nitride platelets are oriented relative to one another in the agglomerates according to the invention essentially without preferential direction, so that the agglomerates according to the invention have largely isotropic properties.
  • the agglomerates according to the invention are free-flowing and readily meterable. With the same proportion of boron nitride, higher heat conductivity values can be obtained in boron nitride polymer composite materials with the agglomerates according to the invention than with non-agglomerated boron nitride powders. With the agglomerates according to the invention, higher fill levels can be obtained in boron nitride / polymer composites than with non-agglomerated powders. Surprisingly, it has been found that agglomerates of good mechanical stability can be produced by the process according to the invention.
  • the mechanical stability of the agglomerates is important because the agglomerates the filling, transport, dosing, compounding and shaping, for example by injection molding, casting or pressing, so themannverabeitung the boron nitride agglomerates to polymer-boron nitride mixtures and polymer Boron nitride composites, as possible without having to survive decomposition. If the agglomerates break down during compounding, there is a risk that the rheological properties of the polymer-boron nitride mixtures will deteriorate and the thermal conductivity in the polymer-boron nitride composites may decrease.
  • the thermal conductivity in filled polymers is not as much direction-dependent as with the use of platelet-shaped fillers, ie, for example, of platelet-shaped boron nitride primary particles.
  • this minimization of the directional dependence succeeds only if the isotropic agglomerates are mechanically stable enough that they survive in particular the compounding step. For pure boron nitride agglomerates this is not the case.
  • the nitride-bonded boron nitride agglomerates according to the invention which have good mechanical stability, the directional dependence of the thermal conductivity in boron nitride polymer composite materials (filled polymers) can be significantly reduced.
  • FIG. 1 shows an SEM image of agglomerates according to the invention according to Example 9 at 100 ⁇ magnification.
  • FIG. 2 shows a SEM image of agglomerates according to the invention according to Example 16 at 100 ⁇ magnification.
  • FIG. 3 shows a SEM image of agglomerates according to the invention according to Example 23 at 100 ⁇ magnification.
  • FIGS. 4 a-c, 5 a-c and 6 a-c show investigations on transverse sections of agglomerates according to the invention (FIGS. 4 a-c: Example 9, FIGS. 5 a-c: Example 16, FIGS. 6 a-c: Example 23).
  • Figures 4a, 5a and 6a show SEM images of cross sections of agglomerates according to the invention embedded in epoxy.
  • the epoxy is dark gray in the shots.
  • the boron nitride is light gray, the binder phase (aluminum nitride) is even lighter.
  • the contour of the investigated agglomerate is shown in FIGS. 4b, 5b and 6b.
  • Figures 4c, 5c and 6c show the associated EDX surface scans for the element aluminum.
  • the brightness of the pixels on the area scans represents the number of counts for the Al- ⁇ line. The brighter the more counts the more aluminum. In black areas there are no counts, so no aluminum. It can be clearly seen from the figures that the bright areas in the agglomerates of FIGS. 4a, 5a and 6a correspond to the corresponding aluminum-rich areas of FIGS. 4c, 5c and 6c.
  • the aluminum is distributed inhomogeneous in the agglomerate. There are no individual crystallites of a secondary phase recognizable. There are aluminum-rich and aluminum-poor areas in the agglomerate.
  • the binding phase can be recognized as needle-shaped or platelet-shaped inclusions in the agglomerate.
  • the aluminum is distributed inhomogeneous in the agglomerate. It can be seen aluminum-free or aluminum-free in addition to the aluminum-rich areas of the secondary phase.
  • the aluminum is homogeneously distributed over a wide range.
  • the right agglomerate contains an aluminum-free area in the core. The tendency was for more aluminum to be detected in near-surface areas of the agglomerates than in the agglomerate core.
  • the boron nitride agglomerates according to the invention are agglomerates of platelet-shaped hexagonal boron nitride primary particles, the hexagonal boron nitride primary particles being connected to one another by means of an inorganic binder phase.
  • the inorganic binder phase comprises at least one nitride and / or oxynitride.
  • nitrides and oxynitrides are preferably compounds of the elements aluminum, silicon, titanium and boron.
  • binder phase compounds examples include aluminum nitride, aluminum numoxinitrid, silicon nitride, silicon oxynitride (e.g., S1 2 N 2 O), titanium nitride, or also mixed nitrides or oxynitrides such as Sialone (for example, S1 3 Al 3 O 3 N 5 ).
  • the binder phase may also comprise boron nitride or boroxynitride. Mixtures of the compounds mentioned are possible.
  • the nitrides and oxynitrides contained in the binder phase are aluminum nitride (A1N) and / or aluminum oxynitride and / or boron nitride.
  • the binder phase particularly preferably contains aluminum nitride and / or aluminum oxynitride.
  • the aluminum oxynitride may have various compositions, for example, the binder phase may be aluminum oxynitride of the compositions and AlsO ö N, but also other stoichiometries are possible.
  • the nitrides and oxynitrides of the binder phase may be amorphous, semi-crystalline or crystalline.
  • the binder phase is crystalline because it allows higher thermal conductivity values to be achieved in the boron nitride polymer composites.
  • the nitridic binder phase may additionally also contain oxidic phases, such as, for example, boron oxide (B 2 O 3 ), aluminum oxide (Al 2 O 3 ), silicon dioxide (SiO 2 ), titanium dioxide (Ti0 2 ), yttria (Y 2 O 3 ), magnesium oxide (MgO), calcium oxide (CaO) and rare earth metal oxides.
  • the binder phase may additionally contain borates, for example aluminum borates or calcium borates.
  • the binder phase may still contain residual carbon or small amounts of carbides as a result of the production.
  • carbon it is also possible for carbon to be present, which is not residual carbon contained in the production process, but also carbon, which may be present, for example, in the form of graphite.
  • the binder phase may also contain metallic impurities, for example as residual amounts of metal binder phase raw materials such as aluminum, silicon or titanium which are not completely converted during the nitriding of the binder phase.
  • the proportion of metallic phases and carbon is preferably less than 10% by weight, more preferably less than 5% by weight, based on the total agglomerate.
  • the binder phase may also contain elemental boron, borides, boron carbide or other carbides such as silicon carbide.
  • the proportion of boron, borides, boron carbide and other carbides is preferably less than 10% by weight, more preferably less than 5% by weight, based on the total agglomerate.
  • the proportion of nitrides and oxynitrides in the binder phase is preferably at least 50% by weight, more preferably at least 80% by weight, based on the total weight of the binder phase.
  • the binder phase is located between the boron nitride primary particles in the agglomerates, it may also be at least partially on the surface of the agglomerates or cover the surface to a large extent.
  • the binder phase binds the boron nitride primary particles in the agglomerate, so that mechanically more stable agglomerates can be obtained compared to binder-free agglomerates.
  • the stability of the agglomerates can be investigated, for example, in ultrasound examinations with simultaneous measurement of the agglomerate size by means of laser granulometry, the agglomerate decaying over time as a result of the action of the ultrasound. The temporal disintegration of the agglomerate size is recorded, with different curves being formed depending on the agglomerate stability. Soft agglomerates disintegrate faster than mechanically more stable agglomerates.
  • the agglomerate density of the agglomerates according to the invention which can be measured by means of geometrical density determination on nitrided powder compacts, is preferably at least 0.3% of the theoretical density.
  • the agglomerates according to the invention can be roundish to spherical or blocky and edged, depending on the production process. Agglomerates prepared by spray-drying retain their roundish to spherical shape even after nitriding. Agglomerates produced by compaction and comminution have a more blocky or brocked, edged or angular shape.
  • the boron nitride primary particles are distributed randomly in the agglomerates according to the invention, it being possible for regions of a local order to exist locally.
  • the boron nitride platelets are oriented relative to one another in the agglomerates according to the invention essentially without preferential direction, so that the agglomerates according to the invention have largely isotropic properties.
  • the isotropy of the boron nitride agglomerates ie the degree of random orientation of the platelet-shaped boron nitride primary particles in the agglomerates according to the invention, can be characterized by the texture index.
  • the texture index of hexagonal boron nitride with isotropic orientation of the platelet-shaped boron nitride primary particles, ie without preferential orientation, is 1.
  • the texture index increases.
  • the agglomerates according to the invention preferably have a texture index of less than 5, preferably less than 3.5.
  • the determination of the texture index is done by X-ray. For this purpose, the ratio of the intensities of the (002) and (100) reflectances measured on X-ray diffraction diagrams is determined and divided by the corresponding ratio value for an ideal, non-textured hBN sample. This ideal ratio can be determined from the JCPDS data and is 7.29.
  • the texture index (TI) can thus be calculated according to the formula
  • the agglomerates of the invention preferably have an average agglomerate size (d 5 o) of 1 mm and less, ⁇ more preferably 500 or less, more preferably 300 ⁇ and less, and more preferably 200 ⁇ and less (wet measurement, Mastersi- zer 2000 Malvern, Germany ).
  • the specific surface area (BET) of the agglomerates according to the invention is preferably 20 m 2 / g and less, more preferably 10 m 2 / g and less. However, the specific surface area may also be at values above 20 m 2 / g.
  • the proportion of the nitridic binder phase in the boron nitride agglomerates according to the invention is preferably at least 0.5% by weight, more preferably at least 1% by weight, more preferably at least 5% by weight and particularly preferably at least 10% by weight.
  • the proportion of the nitridic binder phase in the boron nitride agglomerates according to the invention is preferably not more than 60% by weight, more preferably not more than 50% by weight, in each case based on the total weight of the agglomerates.
  • the mean particle size of the platelet-shaped boron nitride primary particles in the boron nitride agglomerates according to the invention is preferably 1 to 25 ⁇ m, more preferably 1 to 10 ⁇ m.
  • boron nitride starting powder is mixed with binder phase raw materials. From this mixture, granules or shaped articles are produced in a shaping step, which are then subjected to a temperature treatment in a Nitridieratmo sphere. If appropriate, the resulting granules or shaped bodies can subsequently be comminuted and / or fractionated.
  • boron nitride starting powder for producing the boron nitride agglomerates according to the invention it is possible to use hexagonal boron nitride, amorphous boron nitride, partially crystalline boron nitride and mixtures thereof.
  • the mean particle size ds 0 of the boron nitride powder used may be 0.5-50 ⁇ m, preferably 0.5-15 ⁇ m, more preferably 0.5-5 ⁇ m.
  • hexagonal boron nitride powders having an average particle size of 1 ⁇ m, 3 ⁇ m, 6 ⁇ m, 9 ⁇ m and 15 ⁇ m can be used, but higher average particle sizes of up to 50 ⁇ m are also possible.
  • mixtures of different hexagonal boron nitride powders with different particle sizes can be used.
  • the measurement of the average particle size (d 5 o) of the boron nitride powder used is usually carried out by means of laser diffraction (wet measurement, Mastersizer 2000, Malvern).
  • B 2 0 3 -free boron nitride powder and boron nitride powder with lower B 2 0 3 - contents of up to 0.5 parts by weight, but also with higher B 2 0 3 contents of up to 10 wt. and more are used.
  • the binder phase raw materials may be in solid or liquid or pasty form.
  • the mixing of boron nitride starting powder and binder phase raw materials can be carried out, for example, in a mixing drum, in a V mixer, Röhn wheel mixer, a vibrating mill or an Eirich mixer.
  • the homogeneity can be further increased in a subsequent milling step (eg cross beater mill, drum mill, stirred ball mill).
  • the powder mixture can be dry or moistened.
  • the addition of pressing aids and possibly slip aids is also possible.
  • the mixing can also be wet, for example if the subsequent production of the granules takes place via spray-drying or build-up granulation.
  • Shaping may be accomplished by compacting the dry or wetted pulp mixture into sheets or tablets by uniaxial pressing, isostatic pressing or roller compacting. Also possible shaping methods are granulation methods such as spray granulation or build-up granulation. The residual moisture of the moldings or granules produced can be expelled before nitriding by a temperature treatment at about 100 ° C.
  • the dried shaped bodies or granules are subjected to a temperature treatment in a Nitridieratmo sphere, at temperatures of at least 1000 ° C, preferably of at least 1400 ° C, more preferably of at least 1600 ° C.
  • the nitridation atmosphere preferably comprises nitrogen and / or ammonia.
  • the temperature treatment in the Nitridieratmo sphere creates a nitridic binder phase, which connects the boron nitride primary particles together. Through the nitriding step, the degree of crystallization of the primary particles may increase, which is associated with primary particle growth.
  • metal powders are used as binder phase raw materials for producing the nitridic binder phase, preferably selected from the group comprising aluminum, silicon, titanium and mixtures thereof.
  • the metal is converted to the corresponding metal nitride.
  • oxynitrides or mixtures of metal nitrides and oxynitrides are formed in the nitridation.
  • metal compounds in combination with reducing agents are used as binder phase raw materials for producing the nitridic binder phase.
  • the metal compounds used are preferably compounds of the elements aluminum, silicon and titanium, preferably oxides and / or hydroxides such as, for example, aluminum oxide (Al 2 O 3 ), aluminum hydroxide (Al (OH) 3 ), boehmite (AlOOH), silicon dioxide (SiO 2 ). and titanium dioxide (Ti0 2 ). Borates, for example aluminum borate, can furthermore be used as metal compounds.
  • a reducing agent carbon and hydrogen and organic compounds such as polyvinyl butyral (PVB), melamine and methane can be used. If gaseous substances such as, for example, hydrogen or methane are used as the reducing agent, these substances are added to the nitridation atmosphere.
  • the reducing agent necessary for the reduction can already be present in the metal compound, so that the use of additional reducing agents is unnecessary, for example when using aluminum isopropoxide, tetraethyl orthosilicate or titanium isopropoxide as binder raw material.
  • the metal compounds are converted to the corresponding metal nitrides.
  • oxynitrides or mixtures of metal nitrides and oxynitrides are formed in the nitridation, and the binder phase may also contain residues of unreacted oxides.
  • starting materials for the production of boron nitride can be used as binder phase raw materials for producing the nitridic binder phase.
  • the educts for producing boron nitride may be an oxidic boron source such as boric acid (H 3 B0 3 ) and boron oxide (B 2 O 3 ) in combination with a reducing agent such as carbon or hydrogen or organic compounds such as polyvinyl alcohol (PVA), Polyvinyl butyral (PVB), melamine and methane. If gaseous substances such as, for example, hydrogen or methane are used as the reducing agent, these substances are added to the nitridation atmosphere. Furthermore, it is possible to use essentially oxygen-free boron sources, such as, for example, elemental boron, boron carbide and trimethylborate, as starting materials for the production of boron nitride.
  • nitriding materials which solidify during the temperature treatment in the nitridation atmosphere can be used as binder phase raw materials.
  • the nitridic material may be a nitride and / or oxynitride compound of aluminum and silicon, titanium nitride and the rare earth nitrides may also be used, as well as compounds of the sialone group.
  • sintering aids liquid phases such as yttrium oxide, alumina, magnesia, calcia, silica and rare earth oxides can be used. It is also possible to combine the various embodiments with each other, for example, the first can be combined with the fourth embodiment.
  • reaction-bonded embodiments one to three are preferred embodiments, more preferably the embodiments are one and two, the first embodiment is particularly preferred.
  • the shaped bodies or granules are, after the temperature treatment in the nitriding atmosphere, if necessary, broken or fractionated to the desired agglomerate size in a subsequent comminution and / or fractionation step and thus the nitride-bonded agglomerates according to the invention are produced. If the final agglomerate size has already been adjusted during the granulation of the raw materials, for example if the granulation has been carried out by spray-drying or build-up granulation, the comminution step after nitriding is omitted.
  • the target size for the agglomerate size depends mainly on the particular application.
  • a filler for polymers when used as a filler for polymers, for example, it depends on the intended processing technique and the desired degree of filling, wherein the properties of the respective plastic and processing parameters such as viscosity must be taken into account, and can be adapted to the respective application conditions, such as the use as a filler for thermoplastics, as a filler for thermosets, processing by injection molding, extension, casting, embossing or pressing and film production.
  • the BN-based fillers and filler combinations according to the invention with further fillers can be incorporated into different matrix materials. Particularly preferred are polymers such as thermosets, thermoplastics and silicones.
  • thermosets for example, epoxides, crosslinked polyacrylates and polyurethanes can be used as thermoplastics such as polyamide (PA), polyphenylene sulfide (PPS), polycarbonate (PC), polypropylene (PP), thermoplastic elastomers (TPE), thermoplastic polyurethane elastomers (TPU ) and polyetheretherketone (PEEK).
  • PA polyamide
  • PPS polyphenylene sulfide
  • PC polycarbonate
  • PP polypropylene
  • TPE thermoplastic elastomers
  • TPU thermoplastic polyurethane elastomers
  • PEEK polyetheretherketone
  • the polymer-boron nitride composite materials according to the invention are premixed products which are present, for example, in granular form and can be further processed to other materials and shaped bodies by conventional methods, for example by extrusion processes. Also, the moldings thus produced are referred to herein as polymer boron nitride composites.
  • conventional steps such as sieving, screen breaking and sifting can be used.
  • Optionally contained fines can be removed first.
  • the defined comminution of the agglomerates can also be carried out by means of screens, classifier mills, structured roll crushers and cutting wheels. A dry grinding, for example in a ball mill is possible.
  • the boron nitride agglomerates according to the invention can be subjected to further treatments following their preparation.
  • agglomerates with superficial TiO 2 can be produced by an oxidation of agglomerates with TiN-containing binder phase carried out at 500 ° C., superficial SiO 2 in the case of an Si 3 N 4 -containing binder phase, and superficial SiO 2 in an AIN-containing binder phase A1 2 0 3 are generated.
  • polymers for example with polyethylene glycol (PEG), polyvinyl alcohol (PVA), polyvinyl butyral (PVB), polyvinyl pyrrolidone (PVP), copolymers, acrylates, oils or carboxylic acids
  • PEG polyethylene glycol
  • PVA polyvinyl alcohol
  • PVB polyvinyl butyral
  • PVP polyvinyl pyrrolidone
  • copolymers acrylates, oils or carboxylic acids
  • sol-gel systems for example with boehmite sol or SiO 2 sol, or with water-soluble glasses or nanoparticles or surface-modified nanoparticles or mixtures thereof.
  • the listed surface treatments can also be carried out for mixtures of agglomerates according to the invention with other boron nitride fillers.
  • the treatments can be carried out, for example, in the fluidized bed process.
  • the described treatments result in improved coupling of the polymer matrix to the nitride-bonded agglomerates according to the invention.
  • the agglomerates according to the invention can be used as a filler for polymers and processed into polymer-boron nitride composite materials.
  • Mixtures of the agglomerates according to the invention with other known fillers for polymers, such as carbon, graphite, expanded graphite, aluminum oxide, aluminum nitride and silicon dioxide, for example in the form of fibers, spheres or platelets, can also be used for the preparation of the filled polymers.
  • the agglomerates according to the invention can also be used for other applications, for example for the production of sintered bodies.
  • the rollers used have a corrugated surface, whereby the resulting slugs reach a thickness of 0.4 to 1.6 mm.
  • the slugs are shredded.
  • the resulting granules are abandoned under the same process conditions, whereby by bypassing the Siebreibe slugs with a base of about 3 cm 2 and a thickness of 0.4 to 1, 6 mm are obtained.
  • the nitriding of the binder phase is carried out at 2050 ° C for 2 hours in flowing nitrogen atmosphere. It is heated at 17.5 ° C / min until reaching the final temperature of 2050 ° C.
  • the nitride-bound BN flakes obtained are screened to a size of ⁇ 200 ⁇ m.
  • X-ray analysis shows that boron nitride agglomerates contain aluminum nitride, in addition to hexagonal boron nitride as the main phase.
  • the nitride-bonded boron nitride agglomerates ⁇ 200 ⁇ m produced in this way are in a proportion of 40% by volume in epoxy resin and hardener (Epofix, Struers GmbH, Willich, Germany) in the planetary mixer (Speedmixer DAC 150.1, Hauschild, Hamm, Germany) 30 Homogenized at 3000 rpm. The mixture is cured at room temperature for 12 hours and at 80 ° C.
  • thermo conductivity (WLF) is carried out by measuring the variables thermal conductivity a, specific heat capacity c p and density D and is calculated from these quantities according to the equation
  • WLF a * cp * D.
  • the measurement of a and c p is carried out with the Nanoflash LFA 447 (Netzsch, Selb, Germany) on samples of the size 10 * 10 * 2 mm 3 near room temperature.
  • the density is determined by weighing and determining the geometric dimensions of the exactly shaped samples.
  • the obtained thermal conductivity reading is shown in Table 2.
  • the fine fraction ⁇ 100 ⁇ is separated by screening.
  • the agglomerate stability is determined by means of a laser granulometer (Mastersizer 2000 with dispersing unit Hydro 2000S, Malvern,dorfberg, Germany).
  • a solution of a wetting agent in water mixture of 2 ml of a rinsing agent (G 530 Spülfix, BUZIL factory Wagner GmbH & Co.
  • composition of the starting mixture and the nitriding temperature are given in Table 1.
  • hexagonal boron nitride powder having a primary particle size ds 0 of 3 ⁇ (borosilicate NID ® Sl, from ESK Ceramics GmbH & Co. KG, Germany;. Primary particle size measured by laser diffraction (Mastersizer 2000, Malvern, wet measurement)) is mixed with 50 g Aluminum powder (aluminum semolina, grade AS2WA1, Eckart GmbH & Co. KG, Velden, Germany) was mixed and homogenized in a PE bottle on the roller block with grinding balls for 12 hours. The powder mixture is mixed in a roll compactor (RC 100, Powtec GmbH, Remscheid, Germany) compacted.
  • RC 100 Powtec GmbH, Remscheid, Germany
  • the force with which the rollers are pressed together during the compacting process is 49 kN.
  • the rollers used have a corrugated surface, whereby the resulting slugs reach a thickness of 0.4 to 1.6 mm.
  • the slugs are shredded.
  • the resulting granules are abandoned under the same process conditions, whereby by bypassing the Siebreibe slugs with a base of about 3 cm 2 and a thickness of 0.4 to 1, 6 mm are obtained.
  • the nitriding of the binder phase is carried out at 1600 ° C for 2 hours in flowing nitrogen atmosphere. It is heated at 17.5 ° C / min until the final temperature of 1600 ° C is reached. The nitride-bound BN flakes obtained are screened to a size of ⁇ 200 ⁇ m.
  • boron nitride agglomerates contain aluminum nitride, in addition to hexagonal boron nitride as the main phase.
  • Example 1 a sample for determining the thermal conductivity is prepared (with 40 vol .-% of boron nitride agglomerates produced ⁇ 200 ⁇ in epoxy). From the produced nitride bonded BN agglomerates ⁇ 200 ⁇ the fines fraction ⁇ 100 ⁇ is separated by screening. The agglomerate stability is determined by laser granulometry on the sieve fraction 100-200 ⁇ m of the nitride-bonded agglomerates thus obtained, as described in Example 1. The composition of the starting mixture and the nitriding temperature are given in Table 1.
  • Example 2 is repeated except that nitriding is carried out at 1950 ° C for two hours in nitrogen.
  • boron nitride agglomerates contain aluminum nitride, in addition to hexagonal boron nitride as the main phase.
  • composition of the starting mixture and the nitriding temperature are given in Table 1.
  • the composition of the agglomerates, the d 5 o and dgo values of the agglomerate size distribution (mastersizer, wet measurement without ultrasound at the sieve fraction 100-200 ⁇ ), the agglomerate stability of the agglomerates according to the invention and the thermal conductivity of the filled with 40 vol .-% epoxy compounds are listed in Table 2.
  • Example 2 is repeated, but nitriding is carried out at 2050 ° C for two hours flowing in nitrogen.
  • X-ray analysis shows that boron nitride agglomerates contain aluminum nitride, in addition to hexagonal boron nitride as the main phase.
  • composition of the starting mixture and the nitriding temperature are given in Table 1.
  • the composition of the agglomerates, the ds 0 and d 90 values of the agglomerate size distribution (mastersizer, wet measurement without ultrasound at the sieve fraction 100-200 ⁇ ), the agglomerate stability of the agglomerates according to the invention and the thermal conductivity of the filled with 40 vol .-% Epoxy compounds are listed in Table 2.
  • the rollers used have a corrugated surface, whereby the resulting slugs reach a thickness of 0.4 to 1.6 mm.
  • the slugs are shredded.
  • the resulting granules are abandoned under the same process conditions, whereby by bypassing the Siebreibe slugs with a base of about 3 cm 2 and a thickness of 0.4 to 1, 6 mm are obtained.
  • the nitriding of the binder phase takes place at 1600 ° C. for 2 hours in a flowing nitrogen atmosphere. It is heated at 17.5 ° C / min until the final temperature of 1600 ° C is reached.
  • the nitride-bound BN flakes obtained are screened to a size of ⁇ 200 ⁇ m.
  • boron nitride agglomerates contain aluminum nitride, in addition to hexagonal boron nitride as the main phase.
  • a sample for determining the thermal conductivity is prepared (with 40 vol .-% of boron nitride agglomerates produced ⁇ 200 ⁇ in epoxy).
  • composition of the starting mixture and the nitriding temperature are given in Table 1.
  • the composition of the agglomerates, the d 5 o and dgo values of Agglomer- ratieren distribution (Mastersizer, wet measurement without ultrasound at the sieve fraction 100-200 ⁇ ), the agglomerate stability of the agglomerates according to the invention and the thermal conductivity of 40 vol .-% filled Epoxy compounds are listed in Table 2.
  • Example 5 is repeated but nitriding is carried out at 1950 ° C for two hours, flowing in nitrogen.
  • boron nitride agglomerates contain aluminum nitride, in addition to hexagonal boron nitride as the main phase.
  • composition of the starting mixture and the nitriding temperature are given in Table 1.
  • Example 5 is repeated but nitriding is carried out at 2050 ° C for two hours in nitrogen.
  • X-ray analysis shows that boron nitride agglomerates contain aluminum nitride, in addition to hexagonal boron nitride as the main phase.
  • composition of the starting mixture and the nitriding temperature are given in Table 1.
  • the composition of the agglomerates, the ds 0 and d 90 values of the agglomerate size distribution (mastersizer, wet measurement without ultrasound at the sieve fraction 100-200 ⁇ ), the agglomerate stability of the agglomerates according to the invention and the thermal conductivity of the filled with 40 vol .-% Epoxy compounds are listed in Table 2.
  • the rollers used have a corrugated surface, whereby the resulting slugs reach a thickness of 0.4 to 1.6 mm.
  • the slugs are shredded.
  • the resulting granules are abandoned under the same process conditions, whereby by bypassing the Siebreibe slugs with a base of about 3 cm 2 and a thickness of 0.4 to 1, 6 mm are obtained.
  • the nitriding of the binder phase takes place at 1600 ° C. for 2 hours in a flowing nitrogen atmosphere. It is heated at 17.5 ° C / min until the final temperature of 1600 ° C is reached.
  • the nitride-bound BN flakes obtained are screened to a size of ⁇ 200 ⁇ m.
  • Example 2 X-ray analysis reveals aluminum nitride on the obtained boron nitride agglomerates, in addition to hexagonal boron nitride as the main phase.
  • a sample for determining the thermal conductivity is prepared (with 40 vol .-% of boron nitride agglomerates produced ⁇ 200 ⁇ in epoxy).
  • composition of the starting mixture and the nitriding temperature are given in Table 1.
  • the composition of the agglomerates, the d 5 o and dgo values of Agglomer- ratieren distribution (Mastersizer, wet measurement without ultrasound at the sieve fraction 100-200 ⁇ ), the agglomerate stability of the agglomerates according to the invention and the thermal conductivity of 40 vol .-% filled Epoxy compounds are listed in Table 2.
  • Example 8 is repeated except that nitriding is carried out at 1950 ° C for two hours in nitrogen.
  • boron nitride agglomerates contain aluminum nitride, in addition to hexagonal boron nitride as the main phase.
  • the aluminum content is determined by means of an alkaline melt digestion and measurement by means of ICP OES.
  • the aluminum content is measured as the main constituent in the percentage range as follows: coarse or lumpy sample material is to be comminuted with a suitable mill to a particle size ⁇ 150 ⁇ m ( ⁇ 100 mesh).
  • the equipment and procedures used for this purpose should be selected so that the contamination introduced does not affect the accuracy and precision of the measurement.
  • the sample digestion is carried out by an alkaline melt digestion. For this, a partial sample of about 200 mg to 0.01 mg is weighed exactly in a platinum crucible, mixed with about 3 g of sodium / potassium carbonate, covered with a further 2 g of sodium / potassium carbonate and the platinum lid placed. The crucible is heated on the Bunsen burner until a clear melt has formed. The cooled melt is dissolved with 20 ml hydrochloric acid (concentration about 10 mol / L), the solution is transferred to a 250 ml volumetric flask and this is made up to the mark with water.
  • the aluminum concentration of the sample solution is measured by ICP OES.
  • the calibration is performed against matrix-adapted aqueous calibration solutions with known aluminum concentration.
  • the method blind value is determined by applying the same procedure. dur, but without a sample.
  • the aluminum content of the sample is calculated taking into account the volume of the sample solution, the sample weight and the method blank value.
  • a sample for determining the thermal conductivity is prepared (with 40 vol .-% of boron nitride agglomerates produced ⁇ 200 ⁇ in epoxy).
  • nitride bonded BN agglomerates ⁇ 200 ⁇ the fines fraction ⁇ 100 ⁇ is separated by screening.
  • the agglomerate stability is determined by laser granulometry on the sieve fraction 100-200 ⁇ m of the nitride-bonded agglomerates thus obtained, as described in Example 1.
  • the texture index (TI) was determined to be 1.9. This value shows that the agglomerates do not have a strong texture and are largely isotropic.
  • composition of the starting mixture and the nitriding temperature are given in Table 1.
  • composition of the agglomerates which d 5 o and dgo values of the agglomerate sizes distribution (Mastersizer, wet measurement without ultrasound at the sieve fraction 100-200 ⁇ ), the agglomerate stability of the agglomerates according to the invention and the thermal conductivity of the filled with 40 vol .-% Epoxycompounds listed in Table 2.
  • Example 10 is repeated but nitriding is carried out at 2050 ° C for two hours flowing in nitrogen.
  • boron nitride agglomerates contain aluminum nitride, in addition to hexagonal boron nitride as the main phase.
  • composition of the starting mixture and the nitriding temperature are given in Table 1.
  • the composition of the agglomerates, the ds 0 and d 90 values of the agglomerates Rat sizes distribution (Mastersizer, wet measurement without ultrasound at the sieve fraction 100-200 ⁇ ), the agglomerate stability of the agglomerates according to the invention and the thermal conductivity of filled with 40 vol .-% epoxy compounds are listed in Table 2.
  • hexagonal boron nitride powder having a primary particle size ds 0 of 3 ⁇ (borosilicate NID ® Sl, from ESK Ceramics GmbH & Co. KG, Germany;. Primary particle size measured by laser diffraction (Mastersizer 2000, Malvern, wet measurement)) is mixed with 50 g Alumiumpul ver (Grade Standard Pyro MT, Fa. Eckart GmbH & Co. KG, Velden, Germany) mixed and homogenized in a PE bottle on the roller block with grinding balls for 12 hours. With the powder mixture granules are produced in the roll compactor, as described in Example 1. The nitriding of the binder phase is carried out at 1600 ° C for 2 hours in flowing nitrogen atmosphere.
  • nitride-bound BN flakes obtained are screened to a size of ⁇ 200 ⁇ m.
  • X-ray analysis reveals aluminum nitride and the aluminum oxynitride AlgOsN ö on the boron nitride agglomerates obtained, in addition to hexagonal boron nitride as the main phase.
  • Example 2 a sample is prepared to determine the thermal conductivity (with 40% by volume of the prepared boron nitride agglomerates ⁇ 200 ⁇ m in epoxy).
  • composition of the starting mixture and the nitriding temperature are given in Table 1.
  • Example 11 is repeated, but the proportion of aluminum powder (Grade Standard Pyro MT) in the powder mixture for the preparation of the agglomerates and the nitriding temperature are varied as shown in Table 1.
  • X-ray analysis of the resulting boron nitride agglomerates shows aluminum nitride and aluminum oxynitride ⁇ 1 8 0 3 ⁇ 6 , in addition to hexagonal boron nitride as the main phase.
  • Example 16 On the obtained boron nitride agglomerates of Example 16, an Al determination was carried out according to Example 9. The measured value obtained is 23.1 parts by weight.
  • the texture index (TI) was determined to be 1.8. This value shows that the agglomerates do not have a strong texture and are largely isotropic.
  • compositions of the starting mixtures and the nitriding temperatures are given in Table 1.
  • the nitriding of the binder phase is carried out at 1950 ° C for 2 hours in flowing nitrogen atmosphere. It is heated at 17.5 ° C / min until reaching the final temperature of 1950 ° C.
  • the nitride-bound BN flakes obtained are screened to a size of ⁇ 200 ⁇ m.
  • boron nitride agglomerates contain aluminum nitride, in addition to hexagonal boron nitride as the main phase.
  • Example 2 As described in Example 1, a sample for determining the thermal conductivity is prepared (with 40 vol .-% of boron nitride agglomerates produced ⁇ 200 ⁇ in epoxy).
  • composition of the starting mixture and the nitriding temperature are given in Table 1.
  • the composition of the agglomerates, the d 5 o and dgo values of Agglomer- ratieren distribution (Mastersizer, wet measurement without ultrasound at the sieve fraction 100-200 ⁇ ), the agglomerate stability of the agglomerates according to the invention and the thermal conductivity of 40 vol .-% filled Epoxy compounds are listed in Table 2.
  • Example 18 is repeated, but the proportion of aluminum powder (Grade STAPA Alupor SK I-NE / 75) in the powder mixture for producing the agglomerates and the nitriding temperature are varied as indicated in Table 1. X-ray graphitization of the resulting boron nitride agglomerates aluminum nitride prove, in addition to hexagonal boron nitride as the main phase.
  • Example 23 On the obtained boron nitride agglomerates of Example 23, an Al determination was carried out according to Example 9. The measured value obtained is 26.4 parts by weight. At the sieve fraction 100-200 ⁇ of the nitride-bound agglomerates from Example 23, the texture index (TI) was determined, it is 2.7. This value shows that the agglomerates do not have a strong texture and are largely isotropic.
  • the compositions of the starting mixtures and the nitriding temperatures are given in Table 1.
  • hexagonal boron nitride powder having a primary particle size d 5 o of 3 ⁇ borosilicate NID ® Sl, from ESK Ceramics GmbH & Co. KG;. Particle size measured by Mastersizer 2000, Malvern, wet measurement
  • 100 g Ti0 2 nanopowder Hombitech, Sachtleben, Duisburg, Germany
  • the powder mixture is used to prepare granules in the roll compactor, as described in Example 1.
  • the nitriding of the binder phase is carried out at 1950 ° C for 2 hours in flowing nitrogen atmosphere. It is heated at 17.5 ° C / min until reaching the final temperature of 1950 ° C.
  • the nitride-bound BN flakes obtained are screened to a size of ⁇ 200 ⁇ m.
  • Example 1 a sample is prepared to determine the thermal conductivity (with 40% by volume of the prepared boron nitride agglomerates ⁇ 200 ⁇ m in epoxy). At the sieve fraction 100-200 ⁇ m of the nitride-bound agglomerates, the agglomerate stability is determined as described in Example 1.
  • composition of the starting mixture and the nitriding temperature are given in Table 1.
  • Example 25 is repeated, but TiB 2 is used as the Ti-containing binder phase raw material.
  • the average particle size d 5 o of the TiB 2 powder used (ESK GmbH & Co. KG) is 16.5 ⁇ , the proportion of TiB 2 in the powder mixture is 10 wt.
  • the binder phases TiN and TiB 2 were detected in X-ray diffraction studies, in addition to hexagonal boron nitride as the main phase.
  • composition of the starting mixture and the nitriding temperature are given in Table 1.
  • Example 25 is repeated, but Ti powder is used as the binder phase raw material (Fein Gepulvert 98+, No. 1.12379.0250, Merck, Darmstadt, Germany). After nitridation, the binder phases TiN and TiB 2 were detected in X-ray diffraction studies, in addition to hexagonal boron nitride as the main phase. The composition of the starting mixture and the nitriding temperature are given in Table 1.
  • composition of the agglomerates, the ds 0 and d 90 values of the agglomerate size distribution (mastersizer, wet measurement without ultrasound at the sieve fraction 100-200 ⁇ ), the agglomerate stability of the agglomerates according to the invention and the heat conductivity of the filled with 40 vol .-% Epoxy compounds are listed in Table 2.
  • amorphous boron nitride powder having a total oxygen content of 8% by weight (ESK Ceramics GmbH & Co. KG) is mixed with 100 g of TiO 2 nanopowder (Hombitech, Sachtleben, Duisburg, Germany) and placed in a PE bottle The roller block homogenized with grinding balls for 12 hours.
  • the powder mixture is used to prepare granules in the roll compactor, as described in Example 1.
  • the nitriding of the binder phase is carried out at 1950 ° C for 2 hours in flowing nitrogen atmosphere. It is heated at 17.5 ° C / min until reaching the final temperature of 1950 ° C.
  • the nitride-bound BN flakes obtained are screened to a size of ⁇ 200 ⁇ m.
  • the binding phases TiN and TiB 2 were detected, in addition to hexagonal boron nitride as the main phase.
  • Example 1 a sample for determining the thermal conductivity is prepared (with 40 vol .-% of boron nitride agglomerates produced ⁇ 200 ⁇ in epoxy).
  • the agglomerate stability is determined as described in Example 1.
  • composition of the starting mixture and the nitriding temperature are given in Table 1.
  • Example 29 Example 28 is repeated but TiB 2 is used as the Ti-containing binder phase raw material.
  • the mean particle size ds 0 of the TiB 2 powder used (ESK GmbH & Co. KG) is 16.5 ⁇ , the proportion of TiB 2 in the powder mixture is 10 wt.
  • the binder phases TiN and TiB 2 were detected in X-ray diffraction studies, in addition to hexagonal boron nitride as the main phase.
  • composition of the starting mixture and the nitriding temperature are given in Table 1.
  • the composition of the agglomerates, the ds 0 and d 90 values of the agglomerate size distribution (mastersizer, wet measurement without ultrasound at the sieve fraction 100-200 ⁇ ), the agglomerate stability of the agglomerates according to the invention and the thermal conductivity of the epoxy compound filled with 40% by volume are listed in Table 2. Examples 30
  • Example 28 is repeated except that Ti powder is used as the binder phase raw material (Fein Gepulvert 98+, No. 1.12379.0250, Merck, Darmstadt, Germany).
  • the binder phases TiN and TiB 2 were detected in X-ray diffraction studies, in addition to hexagonal boron nitride as the main phase.
  • composition of the starting mixture and the nitriding temperature are given in Table 1.
  • the temperature treatment of the granules is carried out at 1950 ° C for 2 hours in a flowing nitrogen atmosphere. It is heated at 17.5 ° C / min until reaching the final temperature of 1950 ° C.
  • the resulting annealed nitride bound BN flakes are screened to a size of ⁇ 200 ⁇ m.
  • a sample for determining the thermal conductivity is prepared (with 40 vol .-% of boron nitride agglomerates produced ⁇ 200 ⁇ in epoxy).
  • the agglomerate stability is determined as described in Example 1.
  • composition of the starting mixture and the nitriding temperature are given in Table 1.
  • Example 32 550 g of hexagonal boron nitride powder having a primary particle size ds 0 of 3 ⁇ (borosilicate NID ® Sl, from ESK Ceramics GmbH & Co. KG;. Primary particle size measured by laser diffraction (Mastersizer 2000, Malvern, wet measurement)) is mixed with 450 g Aluminum powder from the Al paste (Grade STAPA Alupor SK I-NE / 75, Eckart GmbH & Co. KG, Velden, Germany) mixed and homogenized in a PE bottle on the roller block with grinding balls for 12 hours. With the powder mixture granules are produced in the roll compactor, as described in Example 1.
  • the nitriding of the binder phase is carried out at 1950 ° C for 2 hours in flowing nitrogen atmosphere.
  • the nitride-bound BN flakes obtained are screened to a size of ⁇ 200 ⁇ m.
  • X-ray analysis shows that boron nitride agglomerates contain aluminum nitride in addition to hexagonal boron nitride.
  • Example 1 a sample for determining the thermal conductivity is prepared (with 40 vol .-% of boron nitride agglomerates produced ⁇ 200 ⁇ in epoxy). At the sieve fraction 100-200 ⁇ m of the nitride-bound agglomerates, the agglomerate stability is determined as described in Example 1.
  • composition of the starting mixture and the nitriding temperature are given in Table 1.
  • Examples 33 and 34 were made according to Example 32, varying the amount of binder phase raw material as indicated in Table 1.
  • the conversion of the binder phase raw materials to the nitridic binder phase is carried out according to Example 32 at 1950 ° C.
  • compositions of the starting mixtures and the nitriding temperatures are given in Table 1.
  • the composition of the agglomerates, the d o- 5 and dgo values of the agglomerate size distribution (Mastersizer, wet measurement without ultrasound at the Siebfrak- tion 100-200 ⁇ ), which agglomerate the agglomerates of the invention and the thermal conductivity of the filled with 40 Vol .-% Epoxycompounds are listed in Table 2.
  • 700 g of hexagonal boron nitride powder having a primary particle size d 5 o of 12 ⁇ (ESK Ceramics GmbH & Co. KG; measured primary particle size by laser diffraction (Mastersizer 2000, Malvern, wet measurement)) is (with 300 g of aluminum powder of the Al paste degrees STAPA Alupor SK I-NE / 75, Eckart GmbH & Co. KG, Velden, Germany) and homogenized in a PE bottle on the roller block with grinding balls for 12 hours. With the powder mixture granules are produced in the roll compactor, as described in Example 1. The nitriding of the binder phase is carried out at 1950 ° C for 2 hours in flowing nitrogen atmosphere.
  • the nitride-bound BN flakes obtained are screened to a size of ⁇ 200 ⁇ m.
  • Example 2 a sample is prepared to determine the thermal conductivity (with 40% by volume of the prepared boron nitride agglomerates ⁇ 200 ⁇ m in epoxy).
  • the agglomerate stability is determined as described in Example 1.
  • the composition of the starting mixture and the nitriding temperature are given in Table 1.
  • 1000 g of hexagonal boron nitride powder having a primary particle size ds 0 of 3 ⁇ may be in a PE bottle on a set of rollers with grinding balls 12 hours homogenized. With the powder mixture granules are produced in the roll compactor, as described in Example 1.
  • the temperature treatment of the slugs is carried out at 1600 ° C for 2 hours in a flowing nitrogen atmosphere. It is heated at 17.5 ° C / min until the final temperature of 1600 ° C is reached.
  • the obtained BN slugs are sieved to a size of ⁇ 200 ⁇ m.
  • the boron nitride agglomerates ⁇ 200 ⁇ m produced in this way are incorporated in the planetary mixer (Speedmixer DAC 150.1, Hauschild, Hamm, Germany) for 30 seconds with a proportion of 40% by volume in epoxy resin and hardener (Epofix, Struers GmbH, Willich, Germany) Homogenized at 3000 rpm.
  • the mixture is cured for 12 hours at room temperature and for a further 12 hours at 80 ° C.
  • the agglomerate stability is determined on the sieve fraction 100-200 ⁇ m of the boron nitride agglomerates thus obtained, as described in Example 1.
  • the composition of the starting mixture and the nitriding temperature are given in Table 1.
  • the composition of the agglomerates, the ds 0 and d 90 values of the agglomerate size distribution (Mastersizer, wet measurement without ultrasound at the sieve fraction 100-200 ⁇ ), the agglomerate stability of the agglomerates and the thermal conductivity of the filled with 40 vol .-% Epoxycompounds are in Table 2 listed.
  • Comparative Examples 2 and 3 were produced according to Comparative Example 1, but the temperature treatment was carried out not at 1600 ° C but at 1950 ° C (Comparative Example 2) and at 2050 ° C (Comparative Example 3), each for 2 hours.
  • compositions of the starting mixtures and the nitriding temperatures are given in Table 1.
  • Example 21 Alupor SK 10 90 2050
  • Example 22 Alupor SK 30 70 1600
  • Example 30 Ti powder 10 90 (BN amorphous) 1950
  • Example 31 AIN powder 14 86 1950
  • Example 1 A1N 1.5 136 223 35 2.71
  • Example 8 A1N 39.5 167 259 100 2.04
  • Example 12 A1N / A1 8 0 3 N 6 14.5 141 226 70 2.46
  • Example 14 A1N / A1 8 0 3 N 6 14.5 135 236 50 2.63
  • Example 18 A1N 7.4 121 211 40 2.72
  • Example 19 A1N 14.5 137 217 45 2.49
  • Example 20 A1N 14.5 134 229 45 2.65
  • Example 21 A1N 14.5 131 209 50 3.02
  • Example 30 TiN / TiB 2 13 170 269 70 2.7
  • Example 31 A1N 14 136 215 35 2.29

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PCT/EP2013/055724 2012-05-09 2013-03-19 Bornitrid-agglomerate, verfahren zu deren herstellung und deren verwendung Ceased WO2013167306A1 (de)

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Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2016092951A1 (ja) * 2014-12-08 2016-06-16 昭和電工株式会社 六方晶窒化ホウ素粉末、その製造方法、樹脂組成物及び樹脂シート
WO2016092952A1 (ja) * 2014-12-08 2016-06-16 昭和電工株式会社 六方晶窒化ホウ素粉末、その製造方法、樹脂組成物及び樹脂シート
JP2016522298A (ja) * 2013-06-19 2016-07-28 スリーエム イノベイティブ プロパティズ カンパニー ポリマー／窒化ホウ素化合物から生成される構成部品、かかる構成部品を生成するためのポリマー／窒化ホウ素化合物、及びそれらの使用
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Citations (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5854155A (en) 1996-01-24 1998-12-29 Denki Kagaku Kogyo Kabushiki Kaisha Hexagonal system boron nitride powder
EP0939066A1 (en) 1998-02-16 1999-09-01 Advanced Ceramics Corporation Method for forming high density boron nitride and high density agglomerated boron nitride particles
US6048511A (en) 1996-03-19 2000-04-11 Advanced Ceramics Corporation Method for forming high density boron nitride and high density agglomerated boron nitride particles
US20020006373A1 (en) 2000-05-18 2002-01-17 Clere Thomas M. Agglomerated hexagonal boron nitride powders, method of making, and uses thereof
WO2003013845A1 (en) 2001-08-07 2003-02-20 Saint-Gobain Ceramics And Plastics, Inc. A high solids hbn slurry hbn paste spherical hbn powder, and methods of making and using them
US20040208812A1 (en) 2000-11-28 2004-10-21 Clere Thomas M. Method for making high thermal diffusivity boron nitride powders
WO2005021428A1 (en) 2003-08-21 2005-03-10 Saint-Gobain Ceramics & Plastics, Inc. Boron nitride agglomerated powder
WO2006023860A2 (en) * 2004-08-23 2006-03-02 General Electric Company Thermally conductive composition and method for preparing the same
US20060127422A1 (en) 1999-08-31 2006-06-15 General Electric Company Boron nitride particles of spherical geometry and process for making thereof
US20100226095A1 (en) * 2007-09-26 2010-09-09 Mitsubishi Electric Corporation Heat conductive sheet and power module
US20120046387A1 (en) * 2010-08-19 2012-02-23 Keng Te Chu Slurry for preparing boron nitride aggregates of spherical geometry and application thereof

Family Cites Families (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB742324A (en) * 1952-05-17 1955-12-21 Carborundum Co Improvements in bodies containing boron nitride
US4138252A (en) * 1977-06-10 1979-02-06 Vereschagin Leonid F Cubic boron nitride in a binder and method for its production
JPS6022676B2 (ja) * 1980-02-23 1985-06-03 日本鋼管株式会社 窒化硅素・窒化硼素複合焼結体及びその製造方法
JPH02116616A (ja) * 1988-10-24 1990-05-01 Kawasaki Steel Corp 窒化硼素・窒化アルミニウム複合粉末の製造方法
JP3948632B2 (ja) * 1993-08-12 2007-07-25 独立行政法人産業技術総合研究所 被覆高圧型窒化硼素焼結体及びその製造法
WO2000030996A2 (en) * 1998-11-19 2000-06-02 Vesuvius Crucible Company Composite material
CN101218189B (zh) * 2005-07-15 2013-04-03 住友电工硬质合金株式会社 复合烧结体
CN101028228A (zh) * 2006-03-01 2007-09-05 通用电气公司 含有亚微粒氮化硼颗粒的化妆品组合物
JP5298372B2 (ja) * 2006-06-12 2013-09-25 住友電工ハードメタル株式会社 複合焼結体
CN100432017C (zh) * 2006-07-28 2008-11-12 北京工业大学 快速制备高强度氮化硅-氮化硼可加工陶瓷的方法
US7527859B2 (en) * 2006-10-08 2009-05-05 Momentive Performance Materials Inc. Enhanced boron nitride composition and compositions made therewith
CN101648809B (zh) * 2009-09-25 2012-06-27 哈尔滨工业大学 氮化硼基复合陶瓷透波材料及其制备方法
DE102010050900A1 (de) * 2010-11-10 2012-05-10 Esk Ceramics Gmbh & Co. Kg Bornitrid-Agglomerate, Verfahren zu deren Herstellung und deren Verwendung
CN102093058B (zh) * 2010-12-23 2013-10-23 大连海事大学 一种α-SiAlON/BN 复合陶瓷材料及其制备方法

Patent Citations (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5854155A (en) 1996-01-24 1998-12-29 Denki Kagaku Kogyo Kabushiki Kaisha Hexagonal system boron nitride powder
US6096671A (en) 1996-01-24 2000-08-01 Denki Kagaku Kogyo Kabushiki Kaisha Method of using hexagonal system boron nitride powder
US6048511A (en) 1996-03-19 2000-04-11 Advanced Ceramics Corporation Method for forming high density boron nitride and high density agglomerated boron nitride particles
EP0939066A1 (en) 1998-02-16 1999-09-01 Advanced Ceramics Corporation Method for forming high density boron nitride and high density agglomerated boron nitride particles
US20060127422A1 (en) 1999-08-31 2006-06-15 General Electric Company Boron nitride particles of spherical geometry and process for making thereof
US20020006373A1 (en) 2000-05-18 2002-01-17 Clere Thomas M. Agglomerated hexagonal boron nitride powders, method of making, and uses thereof
US20040208812A1 (en) 2000-11-28 2004-10-21 Clere Thomas M. Method for making high thermal diffusivity boron nitride powders
WO2003013845A1 (en) 2001-08-07 2003-02-20 Saint-Gobain Ceramics And Plastics, Inc. A high solids hbn slurry hbn paste spherical hbn powder, and methods of making and using them
WO2005021428A1 (en) 2003-08-21 2005-03-10 Saint-Gobain Ceramics & Plastics, Inc. Boron nitride agglomerated powder
WO2006023860A2 (en) * 2004-08-23 2006-03-02 General Electric Company Thermally conductive composition and method for preparing the same
US20100226095A1 (en) * 2007-09-26 2010-09-09 Mitsubishi Electric Corporation Heat conductive sheet and power module
US20120046387A1 (en) * 2010-08-19 2012-02-23 Keng Te Chu Slurry for preparing boron nitride aggregates of spherical geometry and application thereof

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
R. F. HILL: "SMTA National Symposium", 18 November 1996, RESEARCH TRIANGLE PARK, N.C., article "Emerging packaging Technologies"

Cited By (10)

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JP2016522298A (ja) * 2013-06-19 2016-07-28 スリーエム イノベイティブ プロパティズ カンパニー ポリマー／窒化ホウ素化合物から生成される構成部品、かかる構成部品を生成するためのポリマー／窒化ホウ素化合物、及びそれらの使用
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US10106413B2 (en) 2014-02-05 2018-10-23 Mitsubishi Chemical Corporation Agglomerated boron nitride particles, production method for agglomerated boron nitride particles, resin composition including agglomerated boron nitride particles, moulded body, and sheet
US20180354793A1 (en) 2014-02-05 2018-12-13 Mitsubishi Chemical Corporation Agglomerated boron nitride particles, production method for agglomerated boron nitride particles, resin composition including agglomerated boron nitride particles, moulded body, and sheet
US10414653B2 (en) 2014-02-05 2019-09-17 Mitsubishi Chemical Corporation Agglomerated boron nitride particles, production method for agglomerated boron nitride particles, resin composition including agglomerated boron nitride particles, moulded body, and sheet
WO2016092951A1 (ja) * 2014-12-08 2016-06-16 昭和電工株式会社 六方晶窒化ホウ素粉末、その製造方法、樹脂組成物及び樹脂シート
WO2016092952A1 (ja) * 2014-12-08 2016-06-16 昭和電工株式会社 六方晶窒化ホウ素粉末、その製造方法、樹脂組成物及び樹脂シート
EP3181627A1 (en) * 2015-12-15 2017-06-21 3M Innovative Properties Company Thermally conductive pressure sensitive adhesive comprising anisotropic boron nitride agglomerates
WO2017105921A1 (en) * 2015-12-15 2017-06-22 3M Innovative Properties Company Thermally conductive pressure sensitive adhesive comprising anisotropic boron nitride agglomerates

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US20150137026A1 (en) 2015-05-21
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