ESD DISSIPATIVE CERAMICS

Abstract: This invention relates to a dense ceramics having ESD dissipative characteristics, tunable volume and surface resistivies in semi-insulative range (10<3> - 10<11> Ohm-cm), substantially pore free, high flexural strength, light colors, for desired ESD dissipation characteristics, structural reliability, high vision recognition, low wear and particulate contamination to be used as ESD dissipating tools, fixtures, load bearing elements, work surfaces, containers in manufacturing and assembling electrostatically sensitive microelectronic, electromagnetic, electro-optic components, devices and systems.

Description: ESD DISSIPATINE CERAMICS This application claims domestic priority from two commonly owned copending United States Provisional Patent Applications, namely U.S.S.Ν. 60/252,295, filed 21 November 2000 and U.S.S.N. 60/303,655, filed 06 July 2000. The disclosures of these two applications are hereby incorporated herein by reference. An extensive background on electrostatic discharge (ESD) may be found on the Internet at the website of the ESD Association, 7900 Turin Road, Building 3, Suite 2, Rome, NY 13440-2069. See "www.esda.org" for this information. A number of ESD dissipating tools and containers have been devised and used to prevent ESD events and protect sensitive microelectronic devices. It is known that the ESD dissipating materials should not be fully insulative, semiconductive, or conductive. Rather such materials should be semi-insulative (having a Volume Resistivity or "Rv" ranging from 10 3 - 10 11 Ohm-cm). For example, ESD dissipating materials have been suggested in manufacturing and testing MR GMR heads and assembling hard disk drives. 1 ' 2 Similarly, ESD dissipating ceramic and carbon loaded polymer tweezers have been used in handling semiconductor parts. The use of semi-insulative ceramics has been reported for some ESD control applications. In general, semi-insulative ceramics were prepared by mixing conductive or semiconductive ceramics with insulative ceramics, which is a similar manufacturing method to those of ESD dissipative polymers. In the past, some semi-insulative materials were prepared for other applications based on the mixing rule. For example, U.S. Patent No. 3,410,728 reports that metal oxide doped stabilized zirconia have both ionic and electric conductivities at elevated temperature. LaCrO 3 doped stabilized zirconia 3 has also been tried for a high temperature electrical conductor. Recently, German Patent No. 3743630 CI (1989) 4 reported that tweezers made out of various ceramics having surface resistances of 10 5 - 10 10 Ohms can be used to hold electrostatically sensitive components to protect against electrostatic discharge. The patent further indicated that partially or fully stabilized, zirconia based ceramics can be used as a base material. However, the patent did not disclose any information about manufacturing process and other physical properties. Japanese Patent Application No. JP62-25404 A (1987) 5 reported that the resistivity of stabilized zirconia can be controlled in the range of 7xl0 2 - 5.5xl0 5 Ohm (the resistance value can not be converted to resistivity without electrode dimensions) at 600°C by adding 5 - 50 mol.% of transition metal oxide (Co O 3 ) for thermistor elements. Again, the patent did not disclose any information about other physical properties. Japanese Patent Application No. JP3-5363 A (1991) reported that ceramic tape guides made from a mixture of TiO 2 (50-99 wt.%) and Al 2 O 3 can be heat treated in various atmosphere to volume resistivities of 10 4 - 10 11 Ohm-cm to protect the magnetic tape drive from electrostatic discharge damage. The tape guide is more resistant against wear due to its higher hardness of 700 - 900 Kg/mm 2 compared to conventional tape guides made out of stainless steel. U.S. Patent No. 5,612,144 (1997) 6 reports that alumina and silicon carbide based ceramics having resistivities of 2x10 6 to 10 10 Ohm/cm 2 can be prepared by adding, nitrides and carbides of Ti, Zr, Hf, Nb and Ta for electrification removing components. U.S. Patent No. 5,830,819 (1998) 7 reported alumina composite ceramics with volume resistivities from lxlO 7 to lxlO 13 Ohm-cm at 25 - 75 °C and an absolute value of the temperature coefficient of volume resistivity (TCR) of not larger than 1.8%/°C can be prepared with additives containing transition metal oxides such as TiO , Cr 2 O 3 , Co 3 O , MnO 2 , NiO, Fe 2 O 3 , and N 2 O 5 for antistatic part such as conveyer arm, handling jig, tweezers for holding wafers. U.S. Patent No. 5,958,813 (1999) 8 reports that semi-insulating aluminum nitride (AIN) sintered body can be made to the resistivity of 10 4 to 10 11 by forming an intergranular phase from at least one oxides of Ti, Ce, Ni, Ta, Y, Er and Yb, or from Si to prepare a member for removing static electricity. Most materials described above are not necessarily structurally reliable for high performance ESD dissipative ceramic tools because of low flexural strength, fracture toughness and residual porosities in their microstructure. PCT Patent Publication No. WO 98/49121 (1998) reports that semiconductive zirconia with good mechanical properties can be prepared using 10 to 40 wt. % oxides of Fe, Co, Ni, and Cr. Japanese Patent Application No. JP8-39441 (1996) reported that tweezers with volume resistivities of 5 x 10 7 to 1 x 10 9 Ohm-cm can be used to hold semiconductor parts to avoid ESD problems. C. Lam (1996) 9 has reported that the ESD dissipative polymers and ceramic tweezers can be used during the manufacturing and handling of MR heads. The test result indicated that tweezers made out of a "doped" zirconia (vendor proprietary) showed the best performance. Japanese Patent Application No. JP 10-296646 A (1998) reported a high strength, zirconia based composite tweezers with flexural strength of greater than 700 MPa and resistivities of 10 6 - 10 9 Ohm-cm. Further, the material showed a residual magnetic flux of up to 14 Gauss. U.S. Patent No. 6,136,232 (2000) reports that some perovskite type oxides can be mixed with stabilized zirconia to prepare electrostatic dissipative ceramics. The patent also describes that other perovskite type oxides react with zirconia to form zirconates, thus not satisfactory for electrostatic dissipative ceramics. The patent though reports only volume resistivities as a key property. U.S. Patent No. 6,274,524 (2001) claims a semiconductive zirconia body formed under oxidative conditions, comprising 60 to 90 weight % of ZrO 2 including stabilizing agent, said zirconia body having no more than 2% by weight Al O 3 , containing greater than 10 weight % to 40 weight % of one kind or more of oxides of Fe, Co, Ni, and Cr as conductivity giving agents, having a three-point flexural strength of at least 580 MPa, and having a volume specific resistance of 10 6 to 10 9 Ohm-cm. The above prior art attempts at control of ESD have not been fully successful in satisfying either current ESD dissipative requirements or the predicted future requirements for ESD dissipative ceramics, for the following reasons: 1. The prior art lacks sufficient high density ESD dissipative ceramic compositions of the prior art to date have not had sufficiently high density (i.e., 97 - 99 % T.D.). This is due to processing techniques used in the prior art, which have not included hot isostatic pressing (hereinafter "HIPing"). The prior art has typically not made hot isostatically pressed (hereinafter "HIPed") materials due to thermochemical instabilities which during a typical HIPing process. The conductivity modifiers employed in the prior art ESD dissipative ceramics often undergo a thermochemical reduction during a HIPing at high temperature (1200° - 1500°C) and high argon pressure (100 - 250 MPa) in a HIP using graphite heating elements. The thermochemical reaction during the HIPing reduces transitional metallic oxides to oxygen deficient metallic oxides by releasing gases (CO 2 or O 2 ) from the body to the surface resulting in bloating and cracking of ceramic bodies. Pressureless sintered ESD dissipative ceramics have a number of pores (pits) on the surfaces and inside of bodies. For instance, sintered ceramics with 99 % TD may have a number of pores of 0.1 - 10 μm diameters. Assuming a square sintered plate with dimensions of 1 cm x 1 cm x 0.25 cm, 99% T.D., and monosized pores of 1 μm diameter the number of exposed pores on the surface are 10 millions. Often these pores trap particulate debris and contaminants inside, thus difficult to clean and act as the source of contamination during the use of such components in clean room environments. Further, the cleaning of ceramics with residual pores is difficult compared to that of substantially pore free ceramics by HIPing. On the other hand, the number of pores on HIPed ceramic plate with the same dimension and 99.9% T.D. would be 1 million reducing the number of defect (residual pores) to 1/10 of the sintered plates. In addition, the residual pores may interact with diamond grits of grinding wheels during the machining into final shapes and dimensions resulting in damaged spots, which is a potential source of particulate debris over the life time of such components. It is, therefore, highly desirable to prepare a ceramic composition which is easy to density by a conventional hot isostatic press (HIP) to achieve fully dense, structurally reliable ceramic components. 2. The prior art lacks sufficient high strength The HIPing also further eliminates strength limiting cavities and pores in ceramic bodies resulting in structurally stronger and more reliable components. It is well known that the flexural strength of ceramic components can be improved after HIPing by greater than 20 % up to over 50 %. Accordingly, HIPing is a preferred processing step to prepare high strength, mechanically reliable components and enable a thinner cross section and complicated shapes. In summary, HIPable ESD dissipative ceramics are advantageous for an improved contamination control in the fab due to the absence of residual pores. 3. The prior art lacks choices of color Modern manufacturing techniques involve a number of automated processing steps. The efficiency of vision system in such an automated manufacturing system is critical. The high productivity of vision system can be achieved by a fast optical recognition from differences in colors and contrast. The color of magnetic recording heads is substantially black due to the color of slider material (AlTiC, a .composite of titanium carbide and alumina). Therefore, a "non-black" ESD dissipative material is highly preferred in order to ensure higher productivity in vision systems. The color of other microelectronic components may vary. Therefor it is desirable to have various color capabilities with ESD dissipative ceramic tools and fixtures. Most prior art ESD dissipative ceramics commercialized to date have been either black or substantially dark. 4. The prior art lacks tunability The proper ESD dissipation for a specific application can be obtained by a material with a specific volume/surface resistivity. However, there exist a number of different applications requiring a broad range of surface resistivities as reported. In the prior art, the control of volume and surface resistivities has been obtained mainly by a compositional variation in ESD dissipation. Therefore, one should prepare various compositions of materials to satisfy various application needs, each of which may require different resistivities. In addition, the amount of resistivity modifier used in forming composites often tends to make appreciable changes in other material properties. The design engineer thus tends to modify the resistivity specification for the application based on test results. Accordingly, there is a need for a material having a tunable resistivity. 5. The prior art lacks sufficient nonmagnetic properties For some applications, especially in GMR head manufacturing, it is desirable to have the lowest magnetic susceptibility of the ESD dissipative material. For other applications to measure electromagnetic performance of microelectronic devices requires no interference from fixtures. Most transition metal based resistivity modifiers exhibit a substantial magnetic susceptibility. It is reported in PCT Publication No. WO 98/49121 that a residual magnetic flux density of up to 16 Gauss is satisfactory for general ESD dissipative applications. However, there is a need for a substantially nonmagnetic material to be used in tools for electromagnetic measurements. Accordingly, for some applications, it is preferable to have an ESD dissipative material made with one or more substantially nonmagnetic resistivity modifiers. The surface resistivity is not the only measure to determine the performance of ESD dissipative materials. In general, it is very desirable to have a fast dissipation of static charges from the contact at the surface. A more precise measure is a charge decay time in ms as described in the literature. PCT Publication No. WO 98/49121 reports that an acceptable decay time from 1000 to 100 V is 0.1 - 20 seconds. Further, they reported that materials outside of that range are not suitable for ESD dissipative ceramics. However, it has been noted that a decay time of less than 0.1 second is preferred for most ESD dissipative applications. 10 Figure 1 illustrates the apparatus employed in the examples to take measurements of transient current of sample materials. Figure 2 illustrates the apparatus employed in the examples to measure the resistance of sample materials in two locations - one stressed and one not stressed. Figure 3 illustrates the apparatus employed in the examples to measure the effect of perturbations on conductivity of sample materials. One object of the present invention to provide ESD dissipative ceramics which are multifunctional, and capable of dissipating static electricity in contact during manufacturing of sensitive microelectronic devices, and uses. It is known that such ESD dissipative materials must have intermediate resistivities. For instance, the surface resistivity should range from 10 3 to 10 11 Ohm-cm, preferably from 10 4 to 10 10 Ohm-cm, more preferably from 10 5 to 10 9 Ohm-cm and most preferably from 10 6 to 10 9 Ohm-cm. These values are desirable in order to dissipate electrostatic charges. The second requirement is the dissipation characteristics. For instance, the charges must be dissipated fast enough through the volume of part. In addition, the material must be sufficiently homogeneous to dissipate the charges evenly to avoid hot spots. Another object of present invention is to provide a tunable resistivity in a material to meet various resistivity needs for a number of applications. A further object of this invention is to provide various colored ESD dissipative ceramics, especially with substantially light colored ceramics. A still another object of this invention is to provide HIP-able ESD dissipative ceramics with substantially lower residual porosity compared to the pressureless sintered ceramics for high mechanical reliability, low contamination, and good machinability. A special object of the current invention is to provide substantially non-magnetic ESD dissipative ceramics for safer uses for various applications of electromagnetic measurements. Accordingly, the present invention is directed to high-density ceramics (i.e., greater than 99% of theoretical density or "TD") suitable for ESD-dissipation applications. In more preferred embodiments, the density of the ceramics is greater than 99.5% of the theoretical density. Such ceramics have a volume resistivity in the range of 10 5 -10 10 ohm-cm, and also have high strength (i.e., greater than 500 MPa). These ceramics are formed by sintering in air and then, if necessary or desired, by hot isostatic pressing ("HIP" or "HIPing") wherein the HIP environment is preferably not oxidizing. A second heat treatment (either sintering and/or HIPing) is designed to produce one of the following results: (1) it may raise the resistance; or (2) it may lower the resistance; such that the volume resistivity shifts (or moves higher or lower) into the range 10 6 -10 9 ohm- cm. I In certain preferred embodiments, the ceramics are prepared from stabilized ZrO 2 , advantageously with one or more conductive or semi-conductive additives selected from the group consisting of metal oxides, metal carbides, metal nitrides, or combinations thereof. Advantageously, component parts made using these ceramics have a decay time of less than 2 sec. In certain preferred embodiments, the ceramics have a hardness greater than 8.5 GPa Nickers; with Klc greater than 4 MPa m "1/2 and contain ZnO, preferably in range 15-25% (vol% of initial reagents) thereby forming a "light " color ceramic. Some preferred embodiments contain ZnO and up to about 10% (vol.) of a transition metal oxide. For example, manganese oxide (1-8 voI%) works well to produce a "dark" colored ceramic. Some preferred embodiments contain SnO 2 , preferably in range 20-80% (vol% of initial reagents). Other preferred embodiments contain ZrC or barium hexaferrite in the range 15-35 vol%. In certain preferred embodiments, the ceramics have an MOR retention of more than 50% after heat treatment in water at 200°-250°C under equilibrium partial pressure. According to another preferred embodiment, there is provided a particulate composite based on Y-TZP product 15 - 40 % ZnO or 15 - 60 % doped-SnO 2 for light colored ESD dissipating ceramics. The terms "light colored" means that the ceramic material is not black or another dark color. Preferred light colored materials are white, off- white, light grey, tan, and the like. Unlike most electrically conductive metals, ceramics exhibit a wide range of electrical conductivities and resistivities. Ceramics are insulative, semiconductive and conductive in its bulk properties. The electrical resistivity can be tailored by doping conductive or semiconductive phases in insulative phases. Accordingly, resistivity modifiers have been widely used to tailor conduction properties of materials. There exist a number of well-known conductive ceramic families for such tailorability. The modifier could be reactive or non-reactive with base materials. Although there is no single ceramic material that completely satisfies the long wish list of properties for ESD dissipation, it is known that zirconia ceramics can satisfy a good number of requirements excluding electrical properties. A number of insulative Y-TZP (yttria partially stabilized tetragonal zirconia polycrystals) parts have been accepted and used for various tools to manufacture magnetic recording heads to date due to its reliable mechanical properties. Other TZPs by other known stabilizers such as rare earth oxides, MgO, CaO, and mixtures thereof may be used as a matrix material. Zirconia is insulative (Rv = 10 13 Ohm-cm) at room temperature. It has been well known that a conductive zirconia composite can be made by dispersing conductive particles to form electrodischarge machinable (or EDMable) compositions. Typically, particulate dispersoids of metallic conductivity are known to be very effective, such as carbides, borides, and suicides resulting in typical resistivities of less than 1 Ohm-cm, which is too low resistivities for optimum ESD dissipation. Conductive oxides have also been tried to optimize the electrical resistivity of zirconia, such as transition metal oxides, Fe 2 O 3 , Co 2 O 3 , NiO, Cr O 3 , etc. It has been reported 11 that 3 - 15 mol.% iron oxide can be doped to yttria-stabilized ceramics to provide an electrical resistivity of ~10 5 Ohm-cm at 250°C. See also Kyocera's Japanese Patent Applications, cited above. However, some oxide additives alter the transformability of Y- TZP, deteriorating the fracture toughness. Transition metal oxides act as colorant in zirconia, forming characteristic dark colors. Thus, these additives are not satisfactory for a white/light colored material. In addition, these transition metal oxides are subjective to thermochemical redox reactions during the high temperature process such as sintering and HIPing. For instance, Fe 2 O 3 in zirconia undergoes a thermochemical reduction during HIPing in inert gas, such as Ar, resulting in the formation of pores or cracking from gas forming reaction. HIPing in oxygen bearing gases prohibits such deleterious reactions but it is not cost effective due to high cost of platinum heating element and special kiln furniture. Both conductive and semiconductive phases can be used as resistivity modifier to tailor the resistivity and dissipation characteristics. Some resistivity modifier can react with Y-TZP to form new phases resulting in insulative properties and/or changing the transformability of Y-TZP. Such modifiers must be avoided. In addition, the resistivity modifier should satisfy an many requirements as possible listed below to be successfully used in various applications: Pressureless sinterability and sinter-HIPability, good machinability, and structural reliability Various colors, preferably a light color Lowest particle generation Tunable ESD properties Lowest corrosion in processing environments, Substantially non-magnetic or strongly magnetic. It has been found that light colored ESD dissipative ceramics can be prepared by dispersing ZnO grains in Y-TZP matrix. Further, doped SnO 2 in Y-TZP is also effective to achieve a light colored material with the desired resistivity. A few dark colored (or black) ESD dissipative ceramics have also prepared by adding LaMnO 3 , LaCrO 3 , ZrC and BaFe 12 Oι 9 in Y-TZP. Magnetic susceptibilities of resistivity modifiers may vary. (The magnetic susceptibility is defined as the ratio of the intensity of magnetism induced in a material to the magnetizing force or intensity to field to which is subjected.) ZnO, SnO 2 , ZrO 2 , Y 2 O 3 , Al 2 O 3 , ZrC and SiC have very low molar magnetic susceptibility of less than 10 "4 ml/mol. On the other hand, Fe 2 O 3 and BaFe 12 O 19 exhibit high molar magnetic susceptibility of greater than 10 "2 ml/mol. Some materials such as LaMnO 3 and LaCrO 3 show medium molar magnetic susceptibility. The modifiers with low magnetic susceptibility is good for applications requiring low electromagnetic interference. On the other hand, modifiers with high magnetic susceptibilities can be used in applications requiring magnetic functions. It has been found that the resistivity of some materials significantly change after HIPing. Further, the resistivities of HIPed ceramics can be controlled to a desired values by a controlled heat treatment in air or controlled atmosphere. Finally, the volume percentages (Nol%) of ingredients disclosed herein are based upon currently available commercial grades of materials. These numbers may be varied if other materials are employed - e.g., nano-size particles would result in lower Nol% values. As described above, the present invention seeks to solve the problems noted above in the prior art ESD dissipative materials. Accordingly, the present invention provides a strong ESD dissipative material, having high density, preferably formed by HIPing, and a choice of colors, particularly lighter colors than black. The ESD dissipative material of the present invention further has "tunable" resistivities, namely selectable during preparation, with mechanical reliability of components, low contaminating surface, and low magnetic susceptibility. Preferably, the ceramic compositions of the present invention have ESD dissipative characteristics, tunable volume and surface resistivities in the semi-insulative range. Preferably, the ceramic compositions of the present invention may also include a small amount (e.g., less than about 2 wt.%) of one or more sintering aids or additives selected from the group consisting of CaO, MgO, SrO, BaO, Al 2 O 3 , Fe 2 O 3 , ΝiO, CuO, SiO 2 , TiO 2 , Νa 2 O, K 2 O, CeO 2 , Y 2 O 3 and mixtures thereof. The amount of additives must be small enough not to alter desirable properties for ESD dissipative ceramics. In some cases, limited amounts of these oxides may be incorporated from raw materials and/or contamination during the powder processing. Preferably, the ceramic compositions of the present invention are substantially pore free, particularly in relative numbers, e.g., more than 90% pore free - based upon pore sizes greater than 0.5 μm. As used herein, the terms "pore free" and "substantially pore free" may also be defined as a relative density greater than 99%, most preferably greater than 99.5%. Preferably, the ceramic compositions of the present invention have high flexural strength. Sinter-HIPed TZP materials with ZnO, SnO , LaMnO 3 , and LaCrO 3 are stronger 1,000, 650, 716, and 1,005 MPa, respectively. Preferably, the ceramic compositions of the present invention have a color lighter than black. As used herein, the preferred "light" color is defined as being lighter than the midpoint of 16 grey scale as defined by ISO. Color can also be measured using a color meter for more quantitative measurements. The ceramic compositions containing ZnO and SnO 2 compositions show light colors, while most others are black or very dark. Preferably, the ceramic compositions of the present invention have a voltage decay time (a measure of the performance of ESD dissipative ceramics) of less than 500 ms, most preferably less than 100 ms. Preferably, the ceramic compositions of the present invention have a low transient current, such as less than 100 mA, most preferably less than 50 mA. As described above, one aspect of the present invention is the formation of ESD dissipating tools using the ceramic compositions of the present invention. The dense product of the present invention comprises TZP as a base component and particulate dispersoids which include at least one selected from conductive or semiconductive oxides, carbides, nitrides, oxycarbides, oxynitride, oxycarbonitrides, and the like. Some resistivity modifiers were doped with additives or pre-alloyed to desired crystalline form and/or resistivities. When the amount of resistivity modifier is greater than greater than 60 vol. %, it is difficult to take advantage of high fracture toughness and flexural strength of TZP. When the amount of conductivity modifier is less than 10 vol. %, it is difficult to achieve the desired dissipating properties. Suitable ranges of resistivity modifiers thus include 15-50, 20-40 and 25-30 vol. % and include ranges that overlap these values. The average particle sizes of all ceramic powders were smaller than 1 μm to achieve a homogeneous microstructure and uniform electrical properties and desired dissipation characteristics. Some pre-alloyed powders were milled in a plastic jar with Y-TZP milling media to obtain desired particle size. Powders were mixed by a wet milling in a plastic jar mill with Y-TZP milling media, followed by drying and granulation. The dense product of the invention is prepared by molding a mixture of Y-TZP powder and conductivity modifier powders into any desired shapes by any molding methods such as dry pressing, slip casting, tape casting, injection molding, extrusion, and gel casting. An organic binder system may be added into the powder mixture to achieve a high green strength for handling, green machining, and to maintain shapes during the densification. The molded ceramics articles are debinderized and sintered in air or desired reactive or inert atmosphere to greater than 95% T.D., preferably to greater than 97% T.D. The sintered ceramics articles can be further densified by hot isostatic pressing in inert gas or oxygen bearing inert gas to full density. The thus obtained sintered or sinter-HIPed ceramic articles exhibits a volume resistivity of from 1 x 10 to 1 x 10 Ohm-cm in ambient temperature resistivities between that of an insulator and that of a semi-conductor. Some resistivity modifiers may react with Y-TZP during sintering and/or HIPing often forming zirconate compounds with very different electrical properties. Such reaction could be much faster at high temperature as these reactions are thermally activated. Thus, it is sometimes very desirable to limit such a deleterious reaction by reducing the densification temperature and times. Another complicating reaction during sintering is that the conductivity modifier could influence the transformability of zirconia grains either stabilizing the Y-TZP grains further or destabilize the Y-TZP grains. In this case, the yttria content in zirconia may be controlled to optimize the transformability or other TZP systems with different stabilizers may be used. The degree of reactions during the sintering significantly vary depending on the particle size, particle size distribution, and densification temperatures. X-ray diffraction was used to determine any detectable chemical reactions during the sintering. HIPing of zirconia is a well established method for eliminating strength limiting pores or cavities. The flexural strength of sintered ceramics are often improved up to 50% compared to that of pressureless sintered ceramics resulting in a major gain in their structural reliability and machinability. Other resistivity modifiers may have a limited reaction with Y-TZP. However, the modifiers may be thermochemically reduced during the typical HIPing in inert gas, e.g., argon or the like, using graphite heating elements. It is well known that such HIPing may thermochemically reduce such compounds releasing gaseous products. Such gas forming reactions limit the densification caused by bloating, swelling, and/or cracking. For instance, most transition oxides, such as Fe 2 O 3 , Co 2 O 3 , NiO, and TiO 2 , suffer from such reactions. Accordingly, it is very desirable to find a thermochemically stable, conductivity modifier to avoid such problems. Alternatively, an oxygen HIPing may be used to avoid such negative reactions. However, the high cost of oxygen HIPing is often undesirable for the manufacture of cost effective products. A number of different ESD dissipation applications require various resistivities ranging from 10 3 to 10 11 Ohm-cm. The conductivity of ceramics can be controlled by adjusting the amount of conductivity modifiers and/or using different ratios of particle sizes of conductivity modifier over base material. Accordingly, various ceramic compositions may be prepared to cover a variable range of conductivities. Therefore, it is very desirable to establish a method to tune (or tailor) the resistivity of a composition by a rather simple heat treatment (or annealing) of ceramics in air or gas atmosphere. In most ceramic systems the resistivity can change depending on the density of charge carriers such as interstitial cations or vacancies. It is known that a different heat treatment of ceramics at high temperature in a known atmosphere from their thermal history (densification' temperature and atmosphere) can change the equilibrium density of charge carriers in ceramic bodies resulting in a different resistivity. The degree of change in a given system has not been studied for most ceramic systems. In addition, various minor impurities in the system may significantly influence such changes. Further, there may be a few different charge carriers active in some ceramic systems. Accordingly, it is very important to establish the control of resistivities by experiments. Most ESD dissipative ceramics tools require machining into precision shapes and dimensions. Therefore, if there is a compositional gradient on the surface of ceramic body the ESD dissipating characteristics may vary. It was found that the volume and surface resistivity fall within an order of magnitude from a sample. Further, the voltage decay time correlates rather well with the surface resistivity in homogeneous material. For instance, a sample with a low surface resistivity (e.g., Rs = 10 6 Ohm/sq.) exhibits a short voltage decay time, i.e., ~50 ms. If there is a macroscopic compositional segregation in the composite, the dissipation behaviors of material may vary depending on the compositional fluctuation. Characterization Methods: Densities of ceramics were measured by the water displacement method with temperature and atmospheric pressure corrections. 12 Microstructure of ceramics were observed by optical and scanning electron microscopes on polished cross-section of samples prepared by a standard polishing procedure. Color of ceramic pieces were measured by Miniscan XE Plus available from Hunter Associates Laboratory, Inc., Reston, VA, using 45°/0° optical geometry and 7.6 mm aperture. X-ray diffraction (XRD) method was used to determine crystalline phases of powders and densified ceramics. Young's modulus, shear modulus and Poisson's ratio of ceramics were measured by a pulse-echo method using ultrasonic transducers. Hardness of ceramics were determined by Vickers hardness method at loadings of 5 to 20 Kgf. The 4-point flexure strength of ceramics were determined by a method specified in ASTM CI 160-90 using 3x4x50 mm type-B specimen. Assuming a WeibuU modulus of about 10, it is estimated that this method reports a flexural strength that is about 20% lower than that found using JIS R 1601-81 (3-point flexure test using 30 mm span). Average strength of 5 to 15 bars were reported. Fracture toughness of ceramics were determined by an indentation crack length method using Vickers indenter at loadings of 10 to 40 Kgf. An indentation crack strength method was also used in some occasions. Volume and surface resistivities (DC) were determined according to methods specified by the ASTM , and others at 10 or 100 V. The surface of ceramics was ground by a diamond wheel and cleaned in a ultrasonic bath prior to the resistivity measurement. As an electrode, type 1215 silver-loaded conductive rubber sheet about 0.55 mm thick made by Chomerics Inc. of Woburn, MA, was used. Voltage decay time is a measure of charge dissipation and is determined by methods described in literature. 14, 15 ' 16 ' Uses of semi-insulating, ESD dissipative materials: The following is a partial list of the many possible uses of the ESD dissipative materials of the present invention. These suggested uses include the following: MR (magnetoresistive) head substrates, Transfer tools for magnetic head manufacturing (lapping, polishing, cleaning), Tools, fixtures, and containers for HGA (head gimbal assembly), HSA (head stack assembly), HDD (hard disk drive) assembly, Tools, fixtures, and containers for wafer handling, processing, cleaning in water, solvents, and with carbon dioxide, Tools, fixtures, and containers for wire bonding, trimming, cutting, Pick-and-place nozzles for IC chip handling, Nozzles for adhesive and solder dispensing, Wafer handling fixtures, end effectors, vacuum chucks, IC handling/test fixtures, Tools, fixtures, and containers for ESD sensitive devices, e.g., CMOS, GaAs, SiGe, InP, and MRAM, MEMS Assembly fixtures for ICs and magnetic heads, Personal tools: tweezers, screw drivers, scissors, blades, Parts for robotic fingers, Tools, fixtures, and containers for electro-optic coating process, Tools, fixtures, and containers for reticles (photo mask), and the like. In fabricating the component parts described above (which is a non-exhaustive list) the ESD dissipative materials of the present invention may be employed as the entire component part, or as a portion thereof. For example, ESD dissipative materials may be shaped into the various components by grinding, machining, or the like - in order to have a component part this is entirely formed from an ESD dissipative material. On the other hand, small portions of the component parts may be all that require an ESD dissipative material to be added thereto. In that case, one or more small machined or ground (or otherwise formed) segments of the ESD dissipative materials of the present invention (note - two or more materials may be combined if desired) would be added to the component part (either permanently or in a replaceable manner) in the critical area requiring ESD protection. Persons having ordinary skill in each respective component art can readily adapt the ESD dissipative materials of the present invention to the specific requirements of each component listed herein, as well as others not recited above. The present invention will be further illustrated with reference to the following examples which aid in the understanding of the present invention, but which are not to be construed as limitations thereof. EXAMPLE 1 "ZnO" A Y-TZP powder containing about 2.8 mol % yttria (YZ110) available from Saint- Gobain Ceramics & Plastics (SGC&P) was mixed in water with varying amounts of zinc oxide available from Zinc Corporation of America in a jar mill with Y-TZP milling media. The surface areas of YZ110 and ZnO powders were 7 and 20 m 2 /g, respectively, prior to milling. The milled powder was granulated by a laboratory method to pressable powder. The powder was uniaxially pressed into steel molds at 40 MPa, and then cold isostatically pressed (or "CIPed") at 207 MPa to form green bodies. The green bodies were sintered at 2°C/min to a desired sintering temperature (1350° - 1500°C) for 1 hr to achieve a sintered density of greater than ~97 % TD (theoretical density). The theoretical density was calculated by a mixing rule based on volume % of ingredients assuming no reaction between two phases during the sintering. Some sintered bodies were HlPed in Ar at 1300°C for 45 min to achieve the full density. All samples were HlPed to greater than 99.5 % T.D., mostly greater than 99.8% T.D. The resulting densified bodies by sintering and sinter-tHPing were measured for density, Young's modulus, hardness, strength, fracture toughness, phase microstructure, volume and surface resistivities, and ESD dissipation (voltage decay) as summarized in Tables 5 and 6. Effect of ZnO content and grain size: Table 5 summarizes volume resistivities as a function of vol. % ZnO in Y-TZP of pressureless sintered samples. It is noted that the resistivities for the ESD dissipation (10 3 < Rv < 10 Ohm-cm) can be achieved by composite materials with 15 - 35 vol. % ZnO and 85 - 65 vol. % Y-TZP. These sintered materials can be prepared to greater than 99% T.D. at 1400°-1450°C for 1 - 2 Hr. in air. Sample No. 16 was prepared with a Y-TZP powder containing 3 mol % yttria (HSY3.0) and sintered at 1250°C, which is 150°C lower temperature than others, to minimize the grain growth of ZnO. It is noted that the volume resistivity of this sample is 5 orders of magnitude lower than Sample No. 2. The present result indicates the fine grain size of conductive phase (ZnO) by low temperature sintering is favorable to achieve a lower resistivity. Further, it is believed that the amount of modifier could be lower by low temperature sintering and reduced grain growth to achieve the same ESD dissipative resistivity. Effect of Annealing temperature and atmosphere: Surprisingly, the resistivity of Sample No. 8 after HIPing at 1350°C/207 MPa for 45 min showed a significant reduction from 7 x 10 11 to 5 x 10 3 Ohm-cm. Samples No. 9 - 14 show the effect of heat treatment (annealing) in air on the resistivity of HlPed 20 vol. % ZnO/YZl lO composites showing the tunability of resistivity by a simple heat treatment. These results further indicate that it is not necessary to prepare various compositions to cover a broad range of resistivities for various ESD dissipative applications. Annealing at different atmospheres (Sample No. 15) also provide additional means to achieve the tunable resistivity with this composition. An over-annealed sample with Rv of 5 x 10 11 Ohm-cm was annealed at 890°C for 5 Hr. in 2% H 2 N 2 atmosphere, resulting in a resistivity of 5 x 10 6 Ohm-cm. This result indicates that the resistivity control of this material is reversible. Accordingly, it is believed that the desired resistivity can be achieved by composition, annealing in air, and/or annealing in a controlled atmosphere. Table 5 S*: pressure ess s nter ng in a r, H**: HIPing in argon Transient current and voltage decay time: Samples of composition 20% and 25% ZnO/YZllO were prepared and were heat treated in air at temperatures in the range 600°-650°C to give the resistivity values shown below. Measurements of transient current were made with the apparatus shown in Figure 1. To make a measurement, the plate (which is part of the charged plate monitor) is charged to a fixed voltage. This loads the plate with about 7 nC of charge at 350 V. This charge is then dissipated to ground by touching the sample with the movable contact. The peak transient current is determined from the peak voltage seen from the current probe by the oscilloscope, which records voltage every nanosecond. Decay time is measured by reading the voltage output of the charged plate monitor on a digital oscilloscope as a function of time. The time for the voltage to fall from 900 V to 100 V is measured from the oscilloscope after initial charging to 1,000 V. Instrument electronics set a limit of 25 ms as the shortest measurable decay time. The following results were obtained: Table 6 Table 7 summarizes properties of 20 vol. % ZnO/YZllO composition after HIPing. The material is highly dense with a relative density of greater than 99.5% T.D. with a light yellow color (lighter than 50% of 16 gray scale), mechanically strong with a flexural strength of the material of 1 GPa, substantially safe with low transient current, and highly dissipative with a decay time from 1,000V to 100V is typically less than 50 ms. Accordingly, the material should be good for the ESD dissipative ceramics. Further, the residual magnetic flux density of this material is substantially negligible due to the absence of Fe, Co, Ni, and Cr-oxides in the composition. Table 7 EXAMPLE 2 "SnO 2 " A Y-TZP powder (HSY3.0) containing about 3 mol % yttria available from Zirconia Sales of America was mixed with varying amount of tin oxide (SnO 2 , T1186) 18 available from SGC&P in ajar mill with Y-TZP milling media. The powder has nominal dopants of 1% Sb 2 O 3 and 0.5% CuO for improved conductivity. Prior to the mixing the doped tin oxide was milled to surface area of ~15 m 2 /g. Surface area of Y-TZP was 7 m 2 /g prior to milling. Another commercial tin oxide powder (available from Alfa Aesar, Ward Hill, MA) milled to a surface area of 12 m 2 /g was also used. The milled powder was granulated by a laboratory method to pressable powder. The powder was uniaxially pressed into steel molds at 40 MPa, and then CIPed at 207 MPa to form green bodies. The green bodies were sintered at 2°C/min to a desired sintering temperature (1400 - 1500°C) for 1 hr to achieve a sintered density of greater than -95 % T.D. The theoretical density was calculated by a mixing rule based on the composition assuming no reaction between two phased during the sintering. Some sintered bodies were HlPed in Ar at 1400°C for 45 min to achieve the full density. The resulting densified bodies by sintering and sinter-HIPing were measured for density, Young's modulus, hardness, strength, fracture toughness, phase microstructure, volume and surface resistivities, and ESD dissipation (voltage decay). The pure SnO 2 is an insulative material. It was confirmed that compositions of 10- 50% SnO 2 /Y-TZP are insulative, Rv = 10 13 Ohm-cm, as shown in Table 9. A limited heat treatment in Ar and N 2 in a tube furnace did not show a significant decrease in the resistivity. The color was remained as light grayish, lighter than 50% of 16 gray scale. A HlPed sample at 1400°C/207 MPa/60 min in Ar turned into a medium gray and showed resistivities of ~10 7 Ohm-cm. Table 9 S*: pressureless sintering in air, H**: HIPing in argon Properties of HlPed 50% doped-SnO 2 /HSY3.0 were measured as summarized below. The material shows light to medium grey. The material is stiffer and harder than those of 20 vol. % ZnO/YZl lO which are similar to those of typical Y-TZP's. In addition, the material is also substantially non-magnetic. Table 10 EXAMPLE 3 "LaMnO 3 " A batch of LaMnO 3 was prepared by the solid-state reaction of an equimolar powder mixture of La 2 O 3 and Mn 2 O 3 at 1400°C for 2 hr in air. The XRD of reaction formed powder indicated a well developed LaMnO 3 , a perovskite family. The reaction formed powder was milled in a plastic jar mill with Y-TZP milling media to BET surface area of 15 m 2 /g. A batch of 30 vol % LaMnO 3 /3 Y-TZP was processed using mixtures of LaMnO 3 and Y-TZP (YZ110, SGC&P, Worcester, MA) followed by the same preparation method described in Example 1. Samples were sintered at 1250° - 1350°C to greater than 98% T.D.. The density of low temperature (1225°C) sintered samples was greater than 97% T.D. Sintered samples were HlPed at 1175° and 1350°C at 207 MPa of argon to full density. The high temperature (1350°C) sinter-HIPed samples show a significant grain growth, formation of reaction phase, lanthanum zirconate (La 2 Zr 2 O ), and a few minor surface cracks. The low temperature HlPed samples show a much smaller grain size and no indication of bloating or cracking. Both sintered and HlPed samples were black. It is reported in U.S. Patent 6,136,232 (2000) that some perovskite-type compounds such as LaMnO 3 and LaFeO 3 are not chemically stable in combinations with partially stabilized zirconias and at typical sintering temperatures form secondary zirconia compounds such as La 2 Zr O thus effecting the phase stability of the remaining zirconia alloy. The present result indicates that LaM O 3 can be successfully used to prepare a composite with Y-TZP with a low temperature sintering. Microstructural observations by SEM from a polished cross section of low temperature sintered sample indicates that the grain size of the material is less than 1 μm. The XRD from a polished cross section also indicated that the majority of tetragonal zirconia was retained with negligible reaction to form lanthanum zirconate (La 2 Zr 2 O 7 ), which is an insulator. The present results indicate that a tough, black ESD dissipative zirconia can be prepared by mixing LaMnO 3 in Y-TZP by a low temperature sintering. Table 11 S*: pressureless sintering in air, H**: HIPing in argon Table 12 The present result is different from others. For instance, Kyocera's Japanese Patent Application indicates the amount of Mn 2 O 3 must be limited to less than 2 Wt. % in order to achieve a good zirconia ceramics. The effect of HIPing on the volume resistivity was also determined. Unlike other materials described in Examples 1 and 2, the volume resistivity of the material was not changed before and after sintering. It is believed that various doped LaMnO 3 and LaBO 3 (B *■= Al, Mn or Co) 19 ' 20 family can be used as semiconductive dispersoids in zirconia. EXAMPLE 4 "LaCrO 3 " A batch of LaCrO 3 was prepared by the solid-state reaction of an equimolar powder mixture of La O 3 and Cr 2 O 3 at 1400°C for 4 hr in air. The XRD of reaction formed powder indicated a well developed LaCrO 3 . The reaction formed powder was milled in a plastic jar mill with Y-TZP milling media to BET surface area of 15 m /g. A batch of 30 vol % LaCrO 3 /3 Y-TZP was processes using mixtures of LaMnO 3 and Y-TZP (HSY-3.0, Zirconia Sales of America, Atlanta, GA) followed by the same preparation method described in Example 1. Samples were sintered at 1450° - 1500°C in air to greater than 97% T.D. and showed a dark green color with a volume resistivity of 9xl0 3 Ohm-cm. Sintered samples were HlPed at 1450°C at 207 MPa of argon to full density. The color of HlPed samples became slightly lighter than that of sintered only. Microstructural observations by SEM from a polished cross section indicate that the grain size of the material is about 1 μm. The XRD from a polished cross section also indicated that the majority of tetragonal zirconia was retained with no measurable reaction to form lanthanum zirconate. The present results indicate that a dense, tough, dark colored ESD dissipative zirconia can be prepared by mixing LaCrO 3 in Y-TZP by sinter-HIPing. Table 13 S*: pressureless sintering in air, H**: HIPing in argon Table 14 The resistivities were measured before and after HIPing. Surprisingly, we have found a significant increase, up to 3 orders of magnitude, in resistivity after HIPing. The thermal annealing in air at 1400°C/60 min in air reproducibly recover the resistivity back to the sintered value as summarized in Table 13. The present finding on the reversible resistivity has not been reported in the literature. U.S. Patent 6,136,232 (2000) reports that complex chromate A x B y CrO 3 can be used to prepare electrostatic dissipative ceramics. Further, it is stated that the material can be HlPed for higher density. However, it was not disclosed that the resistivity of such material drastically changes with HIPing and a need for adjustment of resistivity by the controlled heat treatment. Batches with varying amounts of Y 2 O 3 : 2Y, 2.5 Y, and 3Y (mol. %) were prepared using mixtures of HSY3.0 and DK-1 (0% Y 2 O 3 -ZrO 2 , Zirconia Sales of America) to determine the optimum stabilization of zirconia. The fracture toughness of these compositions are listed in Table 8 showing a higher Kic up to 9 MPam 0 ' 5 of the composite with 2Y-TZP. EXAMPLE 5 - Zirconium Carbide (ZrC) Similarly, ZrC can be mixed with Y-TZP to prepare dense, semi-insulative, ESD dissipative ceramics as listed in Table 16. The semi-insulating compositions were prepared by mixing 10 to 20 vol % of ZrC in Y-YZP (HSY3.0). ZrC does not react with ZrO 2 during the hot pressing at 1550°C / 20 MPa in argon using graphite dies. The color of hot pressed ZrC was black. The resulting composite is stiffer and harder than ZrO 2 . Accordingly, the semi-insulating materials with ZrC is slightly stiffer and harder than Y-TZP can be prepared with ZrC. Table 16 EXAMPLE 6 - Aluminum Nitride (AIN) This example shows another ceramic material - aluminum nitride - that can be heat- treated to be suitable for static dissipation. A 12x12x1 mm square of aluminum nitride was procured from SGCP (Carborundum). Surface resistance was measured to be greater than 10 10 ohms. This is too high to be able to dissipate charge effectively. The sample was then heat treated in argon at 1900°C for 20 minutes and cooled rapidly to room temperature at a rate more than 10°C/minute. The surface resistance was measured again on both sides. It was about 2 x 10 9 ohms, which is in the range suitable for dissipating static electricity. EXAMPLE 7 - Complex Oxides - BaO 6Fe 2 O 3 Complex oxide compounds such as barium hexaferrite (BaO 6Fe 2 O 3 ) can also be mixed with Y-TZP (YZ110) to prepare dense, semi-insulative, ESD dissipative ceramics. The semi-insulating compositions were prepared by mixing 25 vol % of BaO 6Fe 2 O 3 (BaFe 12 O 19 )in Y-YZP (YZ110). The composition can be sintered at 1300° - 1400°C for 1 Hr. in air to greater than 98% TD. The volume resistivity of the sintered disks was 2 x 10 7 Ohm-cm. Barium hexaferrite is known as a strong magnetic material. The sintered composite was easily attracted by a permanent magnet indicating a good retainablilty of BaO 6Fe 2 O 3 phase in fine zirconia matrix. In summary, one can also prepare a strong magnetic, ESD dissipative, zirconia ceramics for potential applications. EXAMPLE 8 - Effect of Perturbations on Conductivity: A 50 mm x 4 mm x 3 mm bar of composition ZrO 2 -20%ZnO was prepared by mixing powders of ZrO 2 -2.6%Y 2 O 3 and ZnO, milling them together, sintering and then hot isostatic pressing, as in the earlier examples. Figure 3 illustrates the test apparatus used herein. The bar was heat treated in air in the range 600° - 700°C and the surface resistance of the bar, as measured with a PRF-912 probe (from ProStat Corporation of Bensonville, IL) was found to be over 100MΩ. One side of the bar was ground. This lowered surface resistance below 1MΩ, as measured with the same probe. Electrodes were then attached with silver paint to two locations on the ground face of the bar about 7mm apart along the length of the bar. The bar with electrodes was loaded into a standard 4-point bending fixture (with supports 40 mm apart on the tension side and 20 mm apart on the compression side) with the electrodes on the compression side. Load was applied to the bar and the resistance between the electrodes was measured. The dependence of resistance R on compressive strain e was found to follow the equation d lnR/5 e = 100. This value is unusually high - for most conductors d lnR/9 e is less than 5. Although the present invention is not limited by theory, it is believed that this behavior results from the fact that only just enough conductor has been added to the insulating zirconia ceramic to make it conductive, and that small perturbations to the material therefore have disproportionately large effects on conductivity. Several applications suggest themselves. Monitoring the resistance of a component made from this class of materials will provide an indication of the stress in the material. For heavily loaded components, this may lead to early detection of incipient failures. Vibrations in the material should produce oscillations in the electrical conductivity and hence may be conveniently detected. In the example, the sample was deliberately fabricated to have a non-uniform conductivity. This was beneficial because the current was forced to go through the most highly stressed region of the sample, thereby maximizing the response. In other situations - e.g., a bar in pure tension - the stress may be more uniform and, hence, there would be no need to make the conductivity non-uniform. In the example, grinding the surface of the sample was used to enhance the conductivity of the sample in one local area. This could also be accomplished by locally reducing the conductive phase by a chemical means - atomic hydrogen for example - or by diffusing in an additive that promotes conductivity in the conductive phase (alumina in zinc oxide, for example), or by locally lowering the concentration of a conductivity inhibitor (lithium oxide in zinc oxide reduces conductivity and the lithium concentration in a lithium doped sample might be reduced by heat treatment in an HC1 atmosphere) Another factor influencing conductivity is the temperature of the specimen. In cases where this varies, it may be advantageous to measure the resistance of the specimen in two locations - one stressed and one not stressed and use the results from the not-stressed area to correct for the influence of temperature (See Figure 2). The case of a beam in flexure allows a slightly different approach: The two resistance sensors are fabricated by locally increasing the conductivity of the material on opposite faces of the beam. If the two resistance sensors are identical, then the ratio of their resistances will be independent of temperature and will be proportional to the bending stress in the beam. EXAMPLE 9 "Low Temperature Degradation (LTD) Resistant ESD Safe Ceramics" Y-TZP has long been known as tougher and stronger than most other ceramics. It's low temperature degradation (LTD) behavior is, though, a significant limitation for some wear resistant applications at low temperature regime (150° - 300°C). The tetragonal zirconia polycrystals (TZP) transform to monoclinic zirconia polycrystals resulting in volume expansion and microcracking at the low temperature regime. Such transformation can be worst in the presence of humidity, especially under equilibrium steam pressure. An accelerated test has been used to determine the LTD behavior of Y-TZPs as described in U.S. Patent 6,069,103, which is hereby incorporated herein by reference. MOR bars were autoclaved at 200° and 250°C under equilibrium steam pressure for 48 hours in an autoclave, followed by 4-point bending strength measurement. Table 16 shows flexural strength of 20 vol. % ZnO/YZl 10 after the autoclave treatments. The results indicate that the resistance to LTD of 20ZnO/YZ110 is significantly better than that of typical Y-TZP (TZ-3 Y, available from Tosoh, Japan). The improved LTD resistance over Y- TZP is desirable using ESD dissipative, zirconia ceramics in degrading environments. Table 17 - Flexural strength after autoclave treatment for 48 hours. EXAMPLE 10 - Low Particle Generation: ESD safe ceramics are often used in clean room processing environments of magnetic heads, semiconductor components, and IC manufacturing. If ESD safe ceramics shed particles during their use, sensitive electronic components might be damaged. In addition, those contaminated particles must be cleaned, resulting in a costly down time of expensive processing equipment. Further, contaminated particles may contribute for latent or delayed damage in finished products, contributing to costly warranty repairs. Therefore, it is very desirable to develop a material with drastically reduced particle generation. In addition, an improved surface finish process of such material is highly desirable for low particle generation. Twenty (20) ZnO/YZl 10 samples of disk and square shapes were tumble finished by rolling in a ten sided mill for 72 hours with quartz or silicon carbide media. Some samples were lapped or polished to smoother surface finish to determine the effect of surface finish on the particle generation. A white light interference microscope, Zygo NewView 100, was used to measure surface roughness (Ra) after this tumble finish treatment. Samples of the 20 ZnO/YZl 10 with various surface finishes were tested with a liquid particle counter (LPC). A sample with 3 x 4 x 25 mm in size (machined MOR bar) and surface finish of 3800 A was used as a baseline. Samples were cleaned using a standard procedure used to clean burnish/glide heads for magnetic disk media. A Crest ultrasonic bath was used to dislodge particles from the samples into water (68kHz for 30 sec). Liquid particle counts were taken from this water using an LS-200 PMS. The results were normalized by surface area of test sample and reported as number of particles per cm 2 . The baseline sample with Ra of greater than 3000 A showed about greater than 600 particles/cm 2 . The treated samples significantly reduced number of particles as a function of surface finish as shown in Table 18. Rougher surfaces typically generate more particles in sliding friction or physical impact applications due to the abrasive nature of the surface and the material used. Decreasing the surface roughness of 20 ZnO/YZl 10 by tumble finish, fine grinding, lapping or polishing reduces its potential for particle generation. Table 18 - LPC results as a function of surface finish. Tumbling is a low cost, industrial process to clean asperities and burrs. Ceramic thread guides are tumble finished to Ra of 100 A. The present results indicate that ESD dissipative ceramics can be prepared to very low LPC by HIPing and optimum surface finish. For instance ESD dissipative, ceramic tweezers tips can be tumble finished to low LPC. EXAMPLE 11: Color Measurements Color measurements were made using two separate methods. First, lightness of color was judged using a 16 level gray scale ranging from white to black. Measurements were also made with a Hunterlab Miniscan XLE colorimeter, made by Hunter Associates Laboratory of Reston, VA. The instrument illuminates the sample target with diffuse illumination and observes the reflected light at an 8 degree angle with a spectrophotometer covering the range 400-700nm. Output from the colorimeter was presented using the CIE 1976 L*a*b* scale, wherein: L* measures lightness and varies between 0 and 100 (100 is white/1 is black); a* measures redness when positive, gray when zero and greenness when negative; b* measures yellowness when positive, gray when zero and blueness.when negative. We noted that the 50% point on the gray scale corresponded to values of L* higher than 50. Table 19 - CIE Measurement Results The first two samples (A and B) were made from the HSY3.0 zirconia source and sample C from YZ 110. The Kyocera sample was a commercially obtained sample. References: The following references are cited herein as background information. To the extent necessary for a full understanding of this invention,, the disclosures of these references are hereby incorporated herein by reference: 1. A.J. Wallash, "Electrostatic Discharge (ESD) in Magnetic Recording: Past, Present and Future," Proc. Of Understanding ESD in Magnetic Recording, IDEMA, pp. 3- 20, 2000. 2. A.J. Wallash, T.S. Hughbamks and S.H. Voldman, "ESD Failure Mechanisms of Inductive and Magnitoresistive Recording Heads," EOD/ESD Symposium 95, 322 - 330 (1995). 3. J. Elston; Z.Mihailovic, M. Roux, "Study of High-temperature Electrical Properties of Zirconia and Lanthanum Chromite Sinters," Proceedings of a Symposium on Magnetohydrodynamic Electrical Power Generation, p. 1061, 389-403, 1966. 4. Popp; V. Wuerttenbe, "Tweezers protecting components against electrostatic discharge - has handling surfaces of non-chafing ceramic of high specific surface resistance" DE 3743630 C, Mar 16, 1989. 5. "Tape Guides and Method of Manufacturing", JP 3-5363 A, Jan. 11, 1999, - Kyocera. 6. N. Shinohara and O.Kita, "Electrification Removing Components", U.S. Patent No. 5,612,144 Mar. 18, 1997. 7. K. Shikada, et al., "Alumina Sintered Product", U.S. Patent 5,830,819 Nov. 3, 1998. 8. H. Aida, Y. Ito, T. Fukutome, and K. Mikami, " Semi-insulating Aluminum Nitride Sintered Body", U.S. Patent No. 5,958,813, Sept. 28, 1999. - Kyocera. 9. C. Lam, "Characterization of ESD Tweezers for Use with Magnetoresistive Recording Heads," EOS/ESD Symposium- 1996, 14-21 (1996). 10. K.J. Kim et al., "Advancements in Inherently Dissipative Polymer (IDP) Alloys Provide New Levels of Clean, Consistent ESD Protection," EOS/ESD Symposium 2000, pp. 132-38, 2000. 11. R.V. Wilhelm, D.S. Howarth, "Iron Oxide-doped Yttria-Stabilized Zirconia Ceramic: Iron Solubility and Electrical Conductivity," Am. Ceram. Soc. Bull., 58 (2) 228 - 32 (1979). 12. N.A. Pratten, "Review, The Precise Measurement of the Density of Small Samples," J. Mater. Sci., 16, 1937-47 (1981). 13. ASTM: D257-93, "Standard Test Method for DC Resistance or Conductance of Insulating Materials". 14. FED. Test Method Std. No. 101, "Electrostatic Properties of Materials," Rev. B, Method 4046, Jan. 1969; Rev. C, Method 4046.1, Oct. 1982, Change Notice 1. 15. N. Jonassen, "Static-Electric Characterization of Semi-insulating Materials," EOS/ESD Symposium EOS-6, 1984. 16. G. Baumgartner, "Electrostatic Decay Measurement, Theory and Applications," EOS/ESD Symposium 95, pp. 265-72, 1995. 17. CF. Lam, C. Chang, "Decay-Time Characterization of ESD Materials for Use with Magnetoresistive Recording Heads," EOS/ESD Symposium 97, pp. 373-81, 1997. 18. E.A. Bush,.U.S. Patent No. 3,502,597, Mar. 24, 1970. - "Method of Improving the Electrical Conductivity of Sintered Tin Oxide Electrodes". 19. M.J. DeBarr, et al., "Conduction Mechanism in the La(Al,Mn) 3 System," Point Defects and Related Properties of Ceramics, Ed. T.O. Mason, et al, Ceramic Trans. Vol 24, Am. Ceram. Soc, pp. 229 - 238, 1991. 20. M.S. Islam, M.Cherry and L.J. Winch, "Defect Chemistry of LaBO 3 (B = La, Mn or Co) Perovskite-type Oxides," J. Chem. Soc, Faraday Trans, 92930479-482 (1996). The present invention has been described in detail, including the preferred embodiments thereof. However, it will be appreciated that those skilled in the art, upon consideration of the present disclosure, may make modifications and/or improvements on this invention and still be within the scope and spirit of this invention as set forth in the following claims.

Claims: CLAIMS 1. An ESD dissipative ceramic composition formed by sintering a mixture comprising a base material and one or more resistivity modifiers for a sufficient time and at a sufficient temperature to achieve at least 99 percent of the theoretical density, wherein the base material comprises a tetragonal zirconia polycrystal (TZP); wherein the resistivity modifier comprises from about 5 vol.% to 60 vol.% of the base material and is selected from the group consisting of conductive and semiconductive materials or mixtures thereof; and wherein the ESD dissipative ceramic composition has the following physical properties: (a) volume resistivity ranging from 10 3 - 10 11 Ohm-cm; (b) flexural strength of at least 500 MPa; and (c) voltage decay time of less than 500 ms. 2. The ESD dissipative ceramic composition of Claim 1, wherein the TZP comprises yttria stabilized TZP (Y-TZP) wherein the yttria is present at from about 2.5 to 4.5 mole percent. 3. The ESD dissipative ceramic composition of Claim 2, wherein the Y-TZP comprises 2.6 mole percent yttria. 4. The ESD dissipative ceramic composition of Claim 2, wherein the Y-TZP comprises 2.8 mole percent yttria. 5. The ESD dissipative ceramic composition of Claim 2, wherein the Y-TZP comprises 3 mole percent yttria. 6. The ESD dissipative ceramic composition of Claim 1, wherein the resistivity modifier comprises from about 10 vol.% to 50 vol.% of the base material. 7. The ESD dissipative ceramic composition of Claim 1, wherein the resistivity modifier comprises from about 20 vol.% to 40 vol.% of the base material. 8. The ESD dissipative ceramic composition of Claim 1, wherein the resistivity modifier comprises from about 25 vol.% to 30 vol.% of the base material. 9. The ESD dissipative ceramic composition of Claim 1, wherein the resistivity modifiers is selected from the group consisting of oxides, carbides, nitrides, oxycarbides, oxynitrides, and oxycarbonitrides. 10. The ESD dissipative ceramic composition of Claim 1, wherein the flexural strength is at least 600 MPa. 11. The ESD dissipative ceramic composition of Claim 1, wherein the flexural strength is at least 700 MPa. 12. The ESD dissipative ceramic composition of Claim 1, wherein the flexural strength is at least 800 MPa. 13. The ESD dissipative ceramic composition of Claim 1, wherein the flexural strength is at least 900 MPa. 14. The ESD dissipative ceramic composition of Claim 1, wherein the flexural strength is at least 1000 MPa. 15. An ESD dissipative component part made from a ceramic of Claim 1 , where the component has less than 600 particles/cm 2 in the particle generation test and where the component has an Ra of less than 3000 A. 16. The ESD dissipative component part of Claim 15, wherein the surface finish is produced by tumbling. 17. The ESD dissipative component part of Claim 15, wherein the color of the ceramic is light. 18. The ESD dissipative component part of Claim 15 , wherein the color of the ceramic is dark. 19. An ESD dissipative ceramic composition formed by sintering a mixture comprising a base material and one or more resistivity modifiers for a sufficient time and at a sufficient temperature to achieve at least 99.5 percent of the theoretical density; wherein the base material comprises a tetragonal* zirconia polycrystal (TZP); wherein the resistivity modifier comprises from about 5 vol.% to 60 vol.% of the base material and is selected from the group consisting of conductive and semiconductive materials or mixtures thereof; and wherein the ESD dissipative ceramic composition has the following physical properties: (a) volume resistivity ranging from 10 5 - 10 9 Ohm-cm; (b) flexural strength of at least 500 MPa; and (c) voltage decay time of less than 500 ms. 20. The ESD dissipative ceramic composition of Claim 19, wherein the TZP comprises yttria stabilized TZP (Y-TZP) wherein the yttria is present at from about 2.5 to 4.5 mole percent. 21. The ESD dissipative ceramic composition of Claim 20, wherein the Y-TZP comprises 2.6 mole percent yttria. 22. The ESD dissipative ceramic composition of Claim 20, wherein the Y-TZP comprises 2.8 mole percent yttria. 23. The ESD dissipative ceramic composition of Claim 20, wherein the Y-TZP comprises 3 mole percent yttria. 24. The ESD dissipative ceramic composition of Claim 19, wherein the resistivity modifier comprises from about 10 vol.% to 50 vol.% of the base material. 25. The ESD dissipative ceramic composition of Claim 19, wherein the resistivity modifier comprises from about 20 vol.% to 40 vol.% of the base material. 26. The ESD dissipative ceramic composition of Claim 19, wherein the resistivity modifier comprises from about 25 vol.% to 30 vol.% of the base material. 27. The ESD dissipative ceramic composition of Claim 19, wherein the resistivity modifiers is selected from the group consisting of oxides, carbides, nitrides, oxycarbides, oxynitrides, and oxycarbonitrides. 28. The ESD dissipative ceramic composition of Claim 19, wherein the flexural strength is at least 600 MPa. 29. The ESD dissipative ceramic composition of Claim 19, wherein the flexural strength is at least 700 MPa. 30. The ESD dissipative ceramic composition of Claim 19, wherein the flexural strength is at least 800 MPa. 31. The ESD dissipative ceramic composition of Claim 19, wherein the flexural strength is at least 900 MPa. 32. The ESD dissipative ceramic composition of Claim 19, wherein the flexural strength is at least 1000 MPa. 33. An ESD dissipative component part made from a ceramic of Claim 19, where the component has less than 600 particles/cm 2 in the particle generation test and where the component has an Ra of less than 3000 A. 34. The ESD dissipative component part of Claim 33, wherein the surface finish is produced by tumbling. 35. The ESD dissipative component part of Claim 33, wherein the color of the ceramic is light. 36. The ESD dissipative component part of Claim 33, wherein the color of the ceramic is dark. 37. An ESD dissipative ceramic composition comprising from about 85 to 60 vol.% Y-TZP and from about 15 to 40 vol.% ZnO densified to at least 95% of the theoretical density by sintering as the primary heat treatment. 38. The ESD dissipative ceramic composition of Claim 37, wherein a secondary heat treatment is employed to increase the theoretical density to greater than 99%. 39. The ESD dissipative ceramic composition of Claim 37, wherein the composition has an L* color measurement of at least 50 using the CIE 1976 L*a*b* scale on an LKE colorimeter. 40. An ESD dissipative ceramic composition comprising from about 90 to 50 vol.% Y-TZP and from about 10 to 50 vol.% semi-conductive SnO 2 densified to at least 95% of the theoretical density by sintering as the primary heat treatment. 41. The ESD dissipative ceramic composition of Claim 40, wherein the composition has an L* color measurement of at least 50 using the CIE 1976 L*a*b* scale on an LKE colorimeter. 42. An ESD dissipative ceramic composition comprising from about 80 to 70 vol.% Y-TZP and from about 20 to 30 vol.% LaMnO 3 densified to at least 95% of the theoretical density by sintering as the primary heat treatment. 43. An ESD dissipative ceramic composition comprising from about 90 to 60 vol.% Y-TZP .and from about 10 to 40 vol.% LaCrO 3 densified to at least 99% of the theoretical density by sintering as the primary heat treatment, followed by hot isostatic pressing as the secondary heat tretment. 44. An ESD dissipative ceramic composition comprising from about 90 to 75 vol.% Y-TZP and from about 10 to 25 vol.% ZrC densified to at least 95% of the theoretical density by sintering as the primary heat treatment, followed by hot isostatic pressing as the secondary heat treatment. 45. An ESD dissipative ceramic composition comprising about 75 vol.% Y-TZP and about 25 vol.% BaO 6Fe 2 O 3 densified to at least 95% of the theoretical density by sintering as the primary heat treatment, followed by hot isostatic pressing as the secondary heat treatment. 46. An ESD dissipative ceramic composition comprising AIN heat treated in argon at 1900°C followed by rapid cooling to room temperature at a rate greater than 10°C/minute. 47. An ESD dissipative ceramic comprising ZrO 2 and semi-conductive SnO 2 , said ceramic having the following physical characteristics: (a) predetermined decay time; (b) hardness greater than 1 OGPa Vickers; and (c) a density of at least 99% of theoretical. 48. An ESD dissipative ceramic composition formed by sintering a mixture comprising a base material and one or more resistivity modifiers; wherein the base material comprises a tetragonal zirconia polycrystal (TZP); wherein the resistivity modifier comprises from about 5 vol.% to 60 vol.% of the base material and is selected from the group consisting of conductive and semiconductive materials or mixtures thereof; and wherein the ESD dissipative ceramic composition has the following physical properties: (a) volume resistivity ranging from 10 6 - 10 9 Ohm-cm; (b) flexural strength of at least 400 MPa; and (c) voltage decay time of less than 500 ms. 49. The ESD dissipative ceramic of Claim 48, wherein the sintering is conducted in air. 50. The ESD dissipative ceramic of Claim 49, wherein a secondary heat treatment step comprises hot isostatic pressing. 51. An ESD dissipative ceramic comprising ZrO 2 and semi-conductive SnO 2 , said ceramic having the following physical characteristics: (a) predetermined decay time; (b) hardness greater than lOGPa Vickers; and (c) an L* color measurement of at least 50 using the CIE 1976 L*a*b* scale on an LKE colorimeter. 52. The ESD dissipative ceramic of Claim 51 , wherein the SnO 2 is present in the range of 20-80% by vol of then initial reagents. 53. A method of processing ESD dissipative ceramics comprising the steps of: (a) consolidating two or more powders to a final density by one or more heat treatments, and (b) using a final heat treatment to produce at least a 25% change in the resistivity of the resulting ceramic. 54. The process of Claim 53, wherein the final heat treatment is conducted in air at less than 90% of the sintering temperature. 55. The process of Claim 53 , wherein the final heat treatment is conducted in oxygen at a partial pressure less than that of atmospheric oxygen. 56. The process of Claim 53, wherein the final heat treatment increases the resistance of the resulting ceramic. 57. The process of Claim 53, wherein the final heat treatment decreases the resistance of the resulting ceramic. 58. The process of Claim 53 , wherein the final heat treatment moves volume resistivity into the range 10 6 -10 9 ohm-cm. 59. A method of forming light colored ESD dissipative ceramics comprising the steps of: (a) forming a mixture comprising from about 85 to 60 vol.% Y-TZP and from about 15 to 40 vol.% ZnO; and (b) densifying the mixture to at least 95% of the theoretical density by a primary heat treatment. 60. The method of Claim 59, further comprising employing a secondary heat treatment step to increase the theoretical density to greater than 99%. 61. A method of forming light colored ESD dissipative ceramics comprising the steps of: (a) forming a mixture comprising from about 90 to 50 vol.% Y-TZP and from about 10 to 50 vol.% semi-conductive SnO 2 ; and (b) densifying the mixture to at least 95% of the theoretical density by a primary heat treatment. 62. The method of Claim 61, further comprising employing a secondary heat treatment step to increase the theoretical density to greater than 99%. 63. A method of modifying the resistivity of ESD dissipative ceramics comprising the step of hot isostatic pressing said ceramics under controlled conditions of heat and atmosphere. 64. A method of forming ceramic-based components for ESD-dissipative purposes comprising the steps of: (a) forming an ESD dissipative ceramic composition; (b) forming the desired surface finish on said ceramic composition; and (c) forming a component, either in whole or in part, from said ESD dissipative ceramic composition. 65. The method of Claim 64, wherein the surface finish is formed by tumbling. 66. The method of Claim 64, wherein the entire component is formed from the ESD dissipative ceramic composition. 67. The method of Claim 64, wherein only a portion of the component is formed from the ESD dissipative ceramic composition. 68. An ESD dissipative component, formed by the method of Claim 64, wherein the component is selected from the group consisting of MR (magnetoresistive) head substrates, transfer tools for magnetic head manufacturing, tools, fixtures, and containers for HGA (head gimbal assembly), HSA (head stack assembly), HDD (hard disk drive) assembly, tools, fixtures, and containers for wafer handling, processing, and cleaning, tools, fixtures, and containers for wire bonding, trimming, cutting, pick-and-place nozzles for IC chip handling, nozzles for adhesive and solder dispensing, wafer handling fixtures, end effectors, vacuum chucks, IC handling and test fixtures, tools, fixtures, and containers for ESD sensitive devices, assembly fixtures for ICs and magnetic heads, tweezers, screw drivers, scissors, blades, parts for robotic fingers, tools, fixtures, and containers for electro- optic coating process, tools, fixtures, and containers for reticles (photo mask). 69. A electrical sensing element formed at least in part from a zirconia-base structural ceramic having a strength of at least 400 MPa, said ceramic further comprising at least 10 vol% ZrO 2 , wherein electrical conductivity of the ceramic is provided by a non- zirconia phase additive. 70. The sensing element of Claim 69, adapted for or service at room temperature. 71. The sensing element of Claim 69 or 70, adapted for measuring temperature, force, or both temperature and force. 72. The sensing element of Claim 69 or 70, where the non-zirconia phase additive comprises ZnO. 73. The sensing element of Claim 69 or 70, where the conductivity of the ceramic is adjusted so that the sensing region(s) is only part of the whole. 74. The sensing element of Claim 69 or 70, where the responses from two or more sensing regions are detected independently. 75. A nonmagnetic ESD dissipative ceramic composition formed by sintering a mixture comprising a base material and one or more nonmagnetic resistivity modifiers; wherein the base material comprises a tetragonal zirconia poly crystal (TZP); wherein the resistivity modifier comprises from about 5 vol.% to 60 vol.% of the base material; and wherein the ESD dissipative ceramic composition has the following physical properties: (a) volume resistivity ranging from 10 6 - 10 9 Ohm-cm; (b) flexural strength of at least 400 MPa; and (c) a residual flux density no greater than about 10 Gauss. 76. The nonmagnetic ESD dissipative ceramic composition of Claim 75, wherein the resistivity modifiers have a molar magnetic susceptibility of less than 10 "3 ml/mol. 77. The nonmagnetic ESD dissipative ceramic composition of Claim 76, wherein the resistivity modifiers are selected from the group consisting of ZnO, SnO 2 , ZrO , Y 2 O 3 , Al 2 O 3 , ZrC, and mixtures thereof.

Inventors: KWON OH-HUN, LIN ROGER J, SIMPSON MATTHEW A, KWON, OH-HUN, LIN, ROGER, J., SIMPSON, MATTHEW, A.
Applicants: SAINT GOBAIN CERAMICS, SAINT-GOBAIN CERAMICS AND PLASTICS, INC.
Application year: 2001
Main classification: C04B35
IPC codes: C04B33, C04B35, G11B5, H05K1