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WO1991008992A1 - Composites ceramiques renforces par barbes de carbure de silicium, et leur procede de fabrication - Google Patents

Composites ceramiques renforces par barbes de carbure de silicium, et leur procede de fabrication Download PDF

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Publication number
WO1991008992A1
WO1991008992A1 PCT/US1990/007276 US9007276W WO9108992A1 WO 1991008992 A1 WO1991008992 A1 WO 1991008992A1 US 9007276 W US9007276 W US 9007276W WO 9108992 A1 WO9108992 A1 WO 9108992A1
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WO
WIPO (PCT)
Prior art keywords
whiskers
coarse
fine
whisker
silicon carbide
Prior art date
Application number
PCT/US1990/007276
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English (en)
Inventor
Aleksander J. Pyzik
Original Assignee
The Dow Chemical Company
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 The Dow Chemical Company filed Critical The Dow Chemical Company
Publication of WO1991008992A1 publication Critical patent/WO1991008992A1/fr

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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
    • 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
    • C04B35/593—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 by pressure sintering
    • 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
    • C04B35/71—Ceramic products containing macroscopic reinforcing agents
    • C04B35/78—Ceramic products containing macroscopic reinforcing agents containing non-metallic materials
    • C04B35/80—Fibres, filaments, whiskers, platelets, or the like

Definitions

  • the present invention generally concerns ceramic composites reinforced by silicon carbide, whiskers.
  • the composites have utility in applications requiring high temperature physical and chemical stability, abrasion wear resistance and resistance to brittle failure.
  • One such application is the cutting or machining of metals.
  • Metal cutting or machining finds extensive application in manufacturing processes. Typical machining operations include shaping, planing, milling, facing, broaching, grinding, sawing, turning, boring, drilling and reaming. Some of these operations, e.g., sawing, act on both internal and external surfaces, whereas others act only on internal surfaces (reaming) or external surfaces (milling).
  • a common productivity measure for machining operations is stated in terms of total amount of metal removed from a work material per unit of time.
  • Parameters specific to cutting tool performance include the material being cut, cutting speed, depth of cut, feed rate and tool life.
  • Tipnis, in "Cutting Tool Wear", Wear Control Handbook, pages 891-893 ? notes that wear is the preferred failure mode for cutting tools. Other failure modes such as fracture, chipping, softening or thermal cracking lead to catastrophic and erratic failures. Although wear is the preferred mode, Tipnis cautions that no predictive tool wear theories are available. As such, the practical approach involves generation and application of tool wear data to balance work material removal rates and economical tool life.
  • Tipnis summarizes basic requirements for a cutting tool as follows: "(a) it must be harder than the material being cut so as to resist forces generated during cutting; (b) it must be tough so as not to fracture under such forces; (c) it must withstand high temperatures generated at the tool-chip interface without deforming; and (d) it must not wear too rapidly.”
  • hot hardness i.e., resistance to softening under temperatures generated at the cutting edge of the tool
  • toughness i.e., resistance to fracture under impacts
  • chemical stability and reactivity i.e., the resistance to dissociation and transformation under temperatures and pressures generated at the cutting edge
  • tendency towards diffusion of elements i.e., resistance to cratering at high cutting temperatures.
  • toughness refers to resistance to premature failure, particularly during initiation of cutting, of a silicon carbide whisker reinforced, ceramic cutting tool. It does not necessarily equate to Kic measured at room temperature according to fracture mechanics definitions of toughness. Cutting performance does not correlate well with data supporting these definitions.
  • M. C. Shaw in Metal Cutting Principles, page 334, (Oxford, 1984), highlights three criteria used in selecting materials for cutting tool applications.
  • the criteria are (a) physical and chemical stability at use temperatures, (b) abrasion wear resistance and (c) resistance to brittle failure. Chemical instability at use temperatures can, for example, destroy tool materials quite rapidly through mechanisms such as melting, excessive diffusion, or a combination of welding and chipping. Shaw suggests, at pages 353-357, that three key physical properties be considered in selecting materials for use as cutting tools.
  • One criterion is strength as measured in four-point- bend testing (Military Standard 1942b).
  • the second criterion is hardness as measured by a Vickers indentor.
  • the third criterion is resistance to fracture.
  • Fracture toughness a commonly used indication of resistance to brittle failure, is measured by the Single Notch Beam Technique or the Chevron Notch Technique. Resistance to crack propagation, or Palmqvist Toughness is determined in conjunction with the hardness test.
  • Satisfactory cutting tool materials must also possess sufficient toughness and strength to withstand mechanical shocks and the like which occur during cutting operations.
  • the composites comprise a matrix of ceramic material having homogeneously dispersed therein 5 to 60 volume percent of silicon carbide whiskers.
  • the whiskers have a monocrystalline structure, a diameter of about 0.6 micrometers and a length of 10 to 80 micrometers.
  • the ceramic material may be alumina, mullite or boron carbide.
  • the present invention is a densified, whisker- -reinforced ceramic composite material comprising a matrix of ceramic material having homogeneously dispersed therein 5 to 40 percent by volume of a bimodal distribution of chemically compatible single crystal whiskers, the whiskers being silicon carbide, silicon nitride, titanium carbide, mullite, titanium diboride, alumina, magnesia or boron nitride, provided, however, that the whiskers are not the same as the ceramic matrix material, the bimodal distribution being based upon relative whisker volume versus whisker width and comprising a volumetric ratio of coarse single crystal whiskers to fine single crystal whiskers of 0.1 to 1, the coarse whiskers having, prior to densification, a number average diameter of greater than or equal to 0.5 but less than 1.0 micrometer and a diameter range of from about 0.1 to 3 micrometers, the fine whiskers having, prior to densification, a number average diameter of greater than or equal to 0.1 but less than 0.5 micrometer and a diameter range of 0.
  • the whiskers are desirably single crystal silicon carbide whiskers.
  • the silicon carbide whiskers used in the present invention are single crystals containing beta and mixed alpha and beta phases of silicon carbide.
  • the whiskers are selected from two distinct average whisker diameter ranges to provide a volume-based, bimodal size j - distribution. Whiskers designated as “coarse whiskers” have a number average whisker diameter within a range of from 0.5 to less than 1.0 micrometer. This represents a diameter range distribution of 0.1 to 3 micrometers. Whiskers designated as "fine whiskers” have an average
  • the graphic portrayal is plotted using a five-point t - smoothing program (0.1 and 0.2 micrometer channel width).
  • polished cross-sections of densified composite material prepared using standard metallographic procedures, are subjected to scanning electron microscopy (SEM) at a
  • a small number of coarse whiskers may, because of the size of such whiskers, occupy a volume equal to that occupied by a much larger number of fine whiskers.
  • a scanning electron micrograph _ of a polished cross-section of a densified composite material prepared from a mixture of alumina and 34 volume percent of SiC whiskers shows that, of 2356 counted, only 77 have a width greater than about 1.4 micrometers.
  • the 77 whiskers account for only 3 percent of the number of whiskers but occupy about 68 percent of whisker volume.
  • the relative volume occupied by coarse whiskers versus that occupied by fine whiskers provides a more accurate picture of whisker distribution than the mere number of such whiskers.
  • bimodal distribution of submicrometer, single crystal silicon carbide whiskers provides an increase in cutting performance over that attainable with the same amount of whiskers selected only from one mode of the distribution.
  • a ten percent, by volume, bimodal distribution provides a- cutting .performance at least as good as a 25 percent, by volume, content of either coarse or fine single crystal silicon carbide whiskers.
  • the single crystal silicon carbide whiskers which provide the bimodal distribution are suitably present in a concentration within a range of 5 to 40 percent by volume, based upon total composite volume.
  • the concentration is desirably 10 to 34 percent by volume.
  • a whisker content of less than five volume percent provides insufficient toughness.
  • a whisker content in excess of forty volume percent leads to processing difficulties, particularly in hot pressing. A solution to such processing difficulties should, however, allow one to use more than forty volume percent.
  • the bimodal distribution suitably has a ratio of coarse whiskers to fine whiskers of 0.3 to 1.0.
  • the ratio is desirably 0.4 to 0.8.
  • the silicon carbide whiskers suitably have an aspect ratio of ten or less.
  • the aspect ratio is desirably 10.
  • Aspect ratios of less than 2.5 provide no advantage and may, in fact, have a considerable disadvantage in that they tend to increase brittleness of the resultant composite.
  • Single crystal silicon carbide whiskers are typically available as mixtures of whiskers with a small amount of particulate silicon carbide. Separation of particles from the whiskers without excessive, loss of whiskers is physically quite difficult. Fortunately, the presence of a small portion of silicon carbide particles does not adversely influence performance of the resultant composite. Care must be taken, however, to avoid an excess of particulate silicon carbide as brittleness, and concurrent likelihood of fracture, increases with an increase in particle loading.
  • Silicon carbide whiskers are believed to be particularly suitable for purposes of the present invention. Satisfactory results may, however, be attained with other whiskers such as those formed from a material selected from the group consisting of silicon nitride, titanium carbide, mullite, titanium diboride, alumina, magnesia or boron nitride.
  • the whiskers should be selected from a chemically compatible material other than that of the matrix. As used herein, "chemically compatible" means that the whiskers and the matrix material do not react to form new phases.
  • the ceramic composites of the present invention are suitably prepared by hot pressing a homogeneous mixture of particulate ceramic material and the two different sizes of silicon carbide whiskers at a pressure and temperature sufficient to provide the composite with a density of greater than about 99 percent of the theoretical density of the ceramic material.
  • the ceramic composites may, if desired, be prepared by hot isostatic pressing or sintering.
  • the bimodal distribution of silicon carbide whiskers and the ceramic powder are desirably in the form of a homogeneous admixture prior to hot pressing.
  • the admixture may be produced by any suitable mixing technique which provides a homogeneous dispersion of the whiskers in the powder and minimizes agglomeration of the ceramic powder, whisker clumping, and whisker breakage.
  • a particularly suitable mixing procedure, especially when the ceramic material is alumina involves the use of an attritor mixer with alumina balls having a size of 3/16 inch (0.48 centimeter) or smaller. Care should be taken during mixing to minimize, if not eliminate, damage or destruction of whiskers.
  • a solution of water, a dispersant and enough ammonium hydroxide to provide a solution pH of about 10.5 is admixed with alumina powder for about 30 minutes at 330 revolutions per minute (rpm) to form a uniform dispersion.
  • Large silicon carbide whiskers wetted with water, a dispersant and a very small amount of ammonium hydroxide are added to the uniform dispersion while mixing continues.
  • Ten minutes after completing addition of the large silicon carbide whiskers, small silicon carbide whiskers wetted with water are added to the dispersion while mixing continues.
  • Two minutes after completing addition of the small whiskers the attritor is stopped and its contents are dumped onto a 30 mesh (550 micrometer) screen to separate the attritor balls.
  • the contents After rinsing the attritor balls and equipment with deionized water, the contents are converted to a dilute slurry with additional deionized water.
  • the dilute slurry is flocculated at a pH of 7.2 with 50 percent nitric acid.
  • the flocculated material is dried in a 100°C. air circulating oven. The dried material is screened with a 60 mesh (250 micrometer) screen to provide a powdered admixture with a maximum agglomerate size of about 100 micrometers.
  • the powdered admixture is formed into a suitable configuration and hot-pressed to a density of greater than about 99 percent of the theoretical density of the ceramic material.
  • Hot pressing may be accomplished in a suitable induction or resistance heated furnace with punches or pressing components formed of graphite or any other suitable material which is capable of withstanding the required pressures and temperatures without adversely reacting with composite constituents.
  • the powdered admixture is poured into a ' graphite die in a shape measuring three inches (7.6 cm) in length by 2.5 inches (6.4 cm) in width by 0.5 inch (1.3 cm) in depth.
  • An initial pressure of 1000 psig (about 70 kg/cm 2 ) is 10 applied to the die while the temperature is raised from ambient to about 1200°C over a period of about 30 minutes. The pressure is then increased to 5000 psig. (about 350 kg/cm 2 ) and maintained at that level while the temperature is increased to 1725°C. over a period of
  • the die is maintained at that temperature and pressure for an additional 45 minutes.
  • the die is then cooled over a two hour period to a temperature of 100°C. with a gradual pressure release at
  • ⁇ r- provide composites in which the whiskers are preferentially aligned and randomly distributed in a plane or axis perpendicular to the hot pressing axis. Satisfactory results are, however, expected with other processes such as hot isostatic pressing and, perhaps,
  • a series of hot-pressed materials are prepared from mixtures of 66 volume percent of alumina (AI2O3) powder (0.8 ⁇ m in size) and 34 volume percent silicon carbide (SiC) whiskers.
  • the mixtures are prepared and hot-pressed using the mixing and hot-pressing procedures set forth hereinabove.
  • the AI2O3 powder is grade RC-HP commercially available from Reynolds Metals Co.
  • the SiC whiskers are nominally coarse, fine or mixtures thereof.
  • the coarse whiskers have an average diameter of 0.94 ⁇ m, an average aspect ratio of about 10.7 (ranging from 1.1 to 77) and are commercially available from American Matrix.
  • the fine whiskers have an average diameter of 0.22 to 0.26 ⁇ m, an average aspect ratio of about 10.6 and are commercially available from Tateho Chemical Industries Co., Ltd.
  • the volume percentages of whiskers and the ratio of large to small whiskers, where both sizes are present, are set forth in Table I together with cutting performance of the resultant compositions.
  • the coarse and fine whiskers are denominated in Table I respectively by letters "C” and "F".
  • the hot-pressed materials are diamond ground into cutting tool inserts- meeting A. .S.I, standards in the RNG 45 style.
  • the cutting edge is chamfered at a 20° angle by 0.003 inch (0.008 cm) width.
  • the insert is tested in a single point turning using a 30 Horsepower Le Blond 1610 Heavy Duty Lathe equipped with a variable speed (DC) drive.
  • the cutting tool is held in place with a Kennametal holder.
  • the cutting tools are tested on an Inconel ® 718 workpiece measuring four inches (10.2 cm) in diameter and twelve inches (30-5 cm) in length and having a hardness of 241 BHN.
  • the workpiece is center drilled with a number 5 combined drill and countersink.
  • the workpiece is held in the lathe by a twelve inch (30.5 cm), three-jaw, self-centering chuck, gripped on 3 inches (7.6cm) of length supported with number 4 Morse taper Nirol live center.
  • the tool holder and quill of the tailstock containing the live center - are all adjusted for minimum overhang to insure maximum rigidity.
  • the machine is run at a cutting speed of 750 feet per minute, a feed rate of 0.007 inches per revolution and a depth of cut of 0.100 inches. No cutting fluid is used. Successive passes are taken and the cutting edge is examined for flank wear and chipping. Testing is terminated after one minute of cutting and cutting performance in terms of uniform wear is measured. The cutting performance is also shown in
  • Example 2 The procedure of Example 1 is duplicated with a different coarse whisker.
  • the coarse whisker has a number average diameter of 0.67 micrometer and an average aspect ratio of 11.0. It is available from American Matrix. Cutting performance of cutting tool inserts prepared as in Example 1 are summarized in Table II.
  • Example 1 The procedure of Example 1 is duplicated with the composition of Sample Number 1-3 to provide a hot- pressed material.
  • the resultant material is examined via SEM in conjunction with the Zeiss-Kontron Image Processing System according to procedure described hereinabove.
  • 2356 whiskers are counted in eleven fields (areas).
  • An additional value for silicon carbide whiskers, denominated as relative volume percent, is determined by the following equation wherein X is DMIN (fiber width) :
  • the relative volume percent represents a given volume percent normalized based upon total volume of whiskers.
  • 15 corresponding to maxima in distribution are 1.0 ⁇ m and 2.4 ⁇ m respectively for fine and coarse whiskers.
  • the volume ratio of coarse to fine whiskers is 0.8.
  • composition of Sample Number 1-3 comprises
  • Example 1 The procedure of Example 1 is replicated except for variations in the volume percentage of silicon -17-
  • Example 1 The hot-pressing procedure of Example 1 is replicated with a different ceramic material.
  • the ceramic material is a mixture of 92 percent silicon nitride, commercially available from UBE Industries under the trade designation UBE-SN-10, 6 percent yttria and two percent of the alumina used in Example 1. All percentages are based upon mixture weight. The amount of whiskers, if any, are shown in Table IV.
  • the resultant hot-pressed materials are diamond ground into cutting tool inserts for comparison with a commercial cutting tool.
  • the inserts are made according to A. .S.I, standards in the SNG 434 style with cutting
  • inserts are tested in a center face milling application using a 40 horsepower Cincinnati #5 single spindle, knee and saddle, vertical milling machine with a 5 horsepower variable speed table.
  • the 0 work material is Class 30 gray cast iron measuring 4 inches (10.2 cm) wide by 12 inches (30.5_ cm) long with a measured hardness of 170 BHN.
  • a one-tooth milling cutter having a 12 inch (30.5 cm) diameter is used with a 5° axial rake, a -5° radial rake and a 15° lead angle.
  • the machine is run at a cutting speed of 3000 surface feet per minute (metric), a 0.60 inch (0.152 cm) depth of cut, and a feed rate of 0.013 inch (0.033 cm) per revolution (or tooth).
  • the center line of the cutter 0 and the center line of the workpiece are coaxial. No cutting fluid is used.
  • Comparative Example C is an unreinforced silicon nitride cutting tool commercially available from Boride Products, Inc. under the trade designation U.S.-20.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Ceramic Engineering (AREA)
  • Manufacturing & Machinery (AREA)
  • Materials Engineering (AREA)
  • Structural Engineering (AREA)
  • Organic Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Cutting Tools, Boring Holders, And Turrets (AREA)
  • Ceramic Products (AREA)

Abstract

L'utilisation d'une distribution bimodale de barbes de carbure de silicium ''grossières'' et ''fines'', à cristal unique et ayant des dimensions inférieures au micromètre pour renforcer les matériaux céramiques permet d'accroître l'efficacité de coupe par rapport au cas où on utilise une quantité équivalente soit de barbes fines, soit de barbes grossières. Les barbes grossières ont un diamètre moyen numérique compris dans une plage allant de 0,5 micromètre à moins de 1,0 micromètre, tandis que les barbes fines ont un diamètre moyen numérique compris dans une plage allant de 0,1 micromètres à 0,5 micromètre. La distribution bimodale des barbes représente de 5 à 40 pour cent en volume du matériau céramique composite résultant renforcé par barbes. Les matériaux ainsi obtenus sont utiles en tant qu'outils de coupe.
PCT/US1990/007276 1989-12-13 1990-12-10 Composites ceramiques renforces par barbes de carbure de silicium, et leur procede de fabrication WO1991008992A1 (fr)

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US45014789A 1989-12-13 1989-12-13
US450,147 1989-12-13

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AU (1) AU7169791A (fr)
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Cited By (8)

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EP0592871A1 (fr) * 1992-10-12 1994-04-20 Sumitomo Electric Industries, Limited Matériau composite céramique et son procédé de fabrication
CN100417618C (zh) * 2006-04-17 2008-09-10 山东大学 原位生长碳化钛晶须增韧氧化铝基陶瓷刀具材料粉末及其制备工艺
CN100417617C (zh) * 2006-04-14 2008-09-10 山东大学 原位生长碳氮化钛晶须增韧氧化铝基陶瓷刀具材料粉末及其制备工艺
CN100448798C (zh) * 2007-04-29 2009-01-07 北京科技大学 一种制备碳化硅晶须增强碳化硅复合材料零件的方法
EP2002694A4 (fr) * 2006-03-30 2009-09-02 Advanced Composite Materials L Matériaux composites et dispositif comprenant un carbure de silicium monocristallin chauffé par rayonnement magnétique
WO2010032137A1 (fr) * 2008-09-17 2010-03-25 Diamond Innovations, Inc. Composites de céramique de nitrure de bore cubique et procédés de fabrication de ceux-ci
US20110169396A1 (en) * 2008-08-08 2011-07-14 Drazenovic Beatrice Semiconductor ceramic
CN111943706A (zh) * 2020-08-21 2020-11-17 齐鲁工业大学 一种添加SiC晶须的自润滑陶瓷刀具及制备方法和应用

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US7731776B2 (en) * 2005-12-02 2010-06-08 Exxonmobil Research And Engineering Company Bimodal and multimodal dense boride cermets with superior erosion performance
CN101348869B (zh) * 2007-07-16 2010-06-02 南京理工大学 晶粒尺寸可控双峰分布的块体超细/纳米晶合金制备方法
CN111170755B (zh) * 2019-12-19 2021-11-19 西安交通大学 一种二硼化钛基纳米复合刀具材料及制备方法
CN116789458B (zh) * 2023-07-06 2024-08-09 肇庆市高要区金祥精细陶瓷有限公司 一种晶须增强的耐火材料及其制备方法

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Cited By (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0592871A1 (fr) * 1992-10-12 1994-04-20 Sumitomo Electric Industries, Limited Matériau composite céramique et son procédé de fabrication
EP2002694A4 (fr) * 2006-03-30 2009-09-02 Advanced Composite Materials L Matériaux composites et dispositif comprenant un carbure de silicium monocristallin chauffé par rayonnement magnétique
US9688583B2 (en) 2006-03-30 2017-06-27 Advanced Composite Materials, Llc Composite materials and devices comprising single crystal silicon carbide heated by electromagnetic radiation
CN100417617C (zh) * 2006-04-14 2008-09-10 山东大学 原位生长碳氮化钛晶须增韧氧化铝基陶瓷刀具材料粉末及其制备工艺
CN100417618C (zh) * 2006-04-17 2008-09-10 山东大学 原位生长碳化钛晶须增韧氧化铝基陶瓷刀具材料粉末及其制备工艺
CN100448798C (zh) * 2007-04-29 2009-01-07 北京科技大学 一种制备碳化硅晶须增强碳化硅复合材料零件的方法
US20110169396A1 (en) * 2008-08-08 2011-07-14 Drazenovic Beatrice Semiconductor ceramic
US9115030B2 (en) * 2008-08-08 2015-08-25 Béatrice Drazenovic Semiconductor ceramic
WO2010032137A1 (fr) * 2008-09-17 2010-03-25 Diamond Innovations, Inc. Composites de céramique de nitrure de bore cubique et procédés de fabrication de ceux-ci
US8354353B2 (en) 2008-09-17 2013-01-15 Diamond Innovations, Inc. Cubic boron nitride ceramic composites and methods of making thereof
CN111943706A (zh) * 2020-08-21 2020-11-17 齐鲁工业大学 一种添加SiC晶须的自润滑陶瓷刀具及制备方法和应用
CN111943706B (zh) * 2020-08-21 2023-03-10 齐鲁工业大学 一种添加SiC晶须的自润滑陶瓷刀具及制备方法和应用

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