Source: http://www.google.com/patents/US7186582?dq=5,371,548
Timestamp: 2014-07-14 00:53:52
Document Index: 237793374

Matched Legal Cases: ['Application No. 60', 'Application No. 60', 'Application No. 60', 'Application No. 60', 'Application No. 60', 'Application No. 60', 'Application No. 60']

Patent US7186582 - Providing a chemical vapor deposition chamber having disposed therein a ... - Google PatentsSearch Images Maps Play YouTube News Gmail Drive More »Sign in<nobr>Advanced Patent Search</nobr>PatentsChemical vapor deposition processes utilize higher order silanes and germanium precursors as chemical precursors. The processes have high deposition rates yet produce more uniform films, both compositionally and in thickness, than films prepared using conventional chemical precursors. In preferred embodiments,...http://www.google.com/patents/US7186582?utm_source=gb-gplus-sharePatent US7186582 - Providing a chemical vapor deposition chamber having disposed therein a substrate:introducing a gas comprised of a higher-order silane of the formula SinH2n+2 and a germanium precursor to the chamber, wherein n=3 6; and depositing a SiGe-containing film onto the substrateAdvanced Patent SearchPublication numberUS7186582 B2Publication typeGrantApplication numberUS 11/124,340Publication dateMar 6, 2007Filing dateMay 6, 2005Priority dateFeb 12, 2001Fee statusPaidAlso published asDE60223662D1, DE60223662T2, DE60227350D1, EP1374290A2, EP1374290B1, EP1374291A2, EP1374291B1, EP1421607A2, US6716713, US6716751, US6743738, US6821825, US6900115, US6958253, US6962859, US7273799, US7285500, US7547615, US7585752, US7893433, US8067297, US8360001, US20020168868, US20020173113, US20020197831, US20030022528, US20030068851, US20030068869, US20030082300, US20050048745, US20050064684, US20050208740, US20050250302, US20070102790, US20080014725, US20080073645, US20100012030, WO2002064853A2, WO2002064853A3, WO2002065508A2, WO2002065508A3, WO2002065516A2, WO2002065516A3, WO2002065516A8, WO2002065517A2, WO2002065517A3, WO2002080244A2, WO2002080244A3, WO2002080244A9Publication number11124340, 124340, US 7186582 B2, US 7186582B2, US-B2-7186582, US7186582 B2, US7186582B2InventorsMichael A. ToddOriginal AssigneeAsm America, Inc.Export CitationBiBTeX, EndNote, RefManPatent Citations (70), Non-Patent Citations (3), Referenced by (4), Classifications (130), Legal Events (2) External Links: USPTO, USPTO Assignment, EspacenetProviding a chemical vapor deposition chamber having disposed therein a substrate:introducing a gas comprised of a higher-order silane of the formula SinH2n+2 and a germanium precursor to the chamber, wherein n=3 6; and depositing a SiGe-containing film onto the substrateUS 7186582 B2Abstract Chemical vapor deposition processes utilize higher order silanes and germanium precursors as chemical precursors. The processes have high deposition rates yet produce more uniform films, both compositionally and in thickness, than films prepared using conventional chemical precursors. In preferred embodiments, trisilane is employed to deposit SiGe-containing films that are useful in the semiconductor industry in various applications such as transistor gate electrodes.
1. A process for depositing a SiGe-containing material onto a surface, comprising:
introducing a gas comprised of a higher-order silane of the formula SinH2n+2 and a germanium precursor to the chamber, wherein n=3�6; and
depositing a SiGe-containing film onto the substrate at a deposition temperature greater than 525� C.
2. The process as claimed in claim 1, wherein the higher-order silane is selected from the group consisting of trisilane and tetrasilane.
5. The process as claimed in claim 1, wherein the SiGe-containing film is at least partially crystalline.
6. The process as claimed in claim 1, wherein the SiGe-containing film is epitaxial.
7. The process as claimed in claim 6, wherein the SiGe-containing film is a strained heteroepitaxial SiGe film.
8. The process as claimed in claim 6, wherein the deposition temperature is in the range of about 620� C. to about 800� C.
9. The process as claimed in claim 1, wherein the SiGe-containing film is amorphous.
10. The process as claimed in claim 1, wherein the SiGe-containing film is polycrystalline.
11. The process as claimed in claim 1, wherein the depositing is carried out at a rate of about 100 Å per minute or higher.
12. The process as claimed in claim 1, wherein the SiGe-containing film is carbon-doped.
13. The process as claimed in claim 1, wherein the gas further comprises a carbon source.
14. The process as claimed in claim 1, wherein the SiGe-containing film comprises a dopant selected from the group consisting of boron, phosphorous, antimony, indium, and arsenic.
15. The process as claimed in claim 1, wherein the gas further comprises a dopant precursor.
16. The process as claimed in claim 1, wherein the chemical vapor deposition chamber is a single-wafer, horizontal gas flow reactor.
17. The process as claimed in claim 1, wherein the SiGe-containing film has a thickness non-uniformity of about 10% or less.
18. The process as claimed in claim 1, wherein the SiGe-containing film has greater uniformity than a comparable film made using silane in place of the higher-order silane.
19. The process as claimed in claim 1, further comprising patterning the SiGe-containing film to form a transistor gate electrode.
20. The process as claimed in claim 1, wherein the substrate comprises a dielectric film.
21. The process as claimed in claim 20, wherein the dielectric film is a silicon oxide film.
22. The process as claimed in claim 20, wherein the dielectric film has a dielectric constant greater than 5.
RELATED APPLICATION INFORMATION This application is a continuation of U.S. patent application Ser. No. 10/074,534, filed on Feb. 11, 2002 now U.S. Pat. No. 6,958,253, which claims priority to: U.S. Provisional Application No. 60/268,337, filed Feb. 12, 2001; U.S. Provisional Application No. 60/279,256, filed Mar. 27, 2001; U.S. Provisional Application No. 60/311,609, filed Aug. 9, 2001; U.S. Provisional Application No. 60/323,649, filed Sep. 19, 2001; U.S. Provisional Application No. 60/332,696, filed Nov. 13, 2001; U.S. Provisional Application No. 60/333,724, filed Nov. 28, 2001; and U.S. Provisional Application No. 60/340,454, filed Dec. 7, 2001; all of which are hereby incorporated by reference in their entireties. This application is also related to and incorporates by reference in their entireties, co-owned U.S. patent application Ser. No. 10/074,563 (now U.S. Pat. No. 6,821,825); Ser. No. 10/074,149 (now U.S. Pat. No. 6,716,751); Ser. Nos. 10/074,722; 10/074,633; and Ser. No. 10/074,564.
FIG. 2 illustrates a gate stack in accordance with a preferred embodiment.
A variety of silicon- and germanium-containing chemical precursors can be suitably used in the film deposition processes disclosed herein to provide Si-containing films, Ge-containing films and alloy films that contain both Si and Ge, e.g., silicon germanium (SiGe, without implying stoichiometry) films. These chemical precursors may also be used in conjunction with carbon sources to provide alloy films, e.g., SiC and SiGeC (without implying stoichiometry) alloy thin films. Preferred Si-containing chemical precursors suitable for use in the instant invention include higher-order, non-halogenated hydrides of silicon, particularly silanes of the formula SinH2n+2 where n=2�6. Particular examples include disilane (H3SiSiH3), trisilane (H3SiSiH2SiH3), and tetrasilane (H3SiSiH2SiH2SiH3). Trisilane (also represented by Si3H8) is most preferred for achieving a balance of volatility and reactivity. Substantially or nearly mass transport limited deposition, at relatively low temperatures, is preferred (but not necessary) for SiGe deposition. Preferred Ge-containing chemical precursors suitable for use in the instant invention include higher-order germanes of the formula GenH2n+2 where n=2�3. In other arrangements, the germanium source can comprise (H3Ge)(GeH2)x(GeH3), where x=0�2. Particular examples include digermane (H3GeGeH3), trigermane (H3GeGeH2GeH3) and tetragermane (H3GeGeH2GeH2GeH3).
In a preferred embodiment, the chemical precursors are used in conjunction with a source of carbon. Preferred carbon sources include silylmethanes [(H3Si)4-xCRx] where x=0�3 and R=H and/or D. The preferred silylmethanes are disilylmethane, trisilylmethane and tetrasilylmethane (x=0�2), with tetrasilylmethane being most preferred. Additional preferred carbon sources include hydrocarbons such as methane, ethane, propane, butanes, etc.; carbon monoxide, carbon dioxide and HCN. These chemical precursors and carbon sources may be purchased from commercial sources or synthesized by methods known to those skilled in the art. Si-containing films such as SiC, SiNC and SiOC (none of which short forms imply particular stoichiometries) have a variety of uses in the semiconductor manufacturing industry, e.g., as etch stop layers, hard masks, and passivation layers.
At temperatures in or near the mass transport limited regime, it has been found that the deposition efficiency of trisilane is advantageously high. In some cases, e.g., as demonstrated in working Examples 1�4 below, the efficiency is so high that non-uniform films (thicker at the edge than in the middle) may result when deposition is conducted at relatively low feed gas flow rates, e.g., feed gas rates typical for silane deposition. This invention is not limited by any theory of operation, but it is believed that, when deposition efficiency is high and the feed gas contacts one part of the substrate before another, at low flow rates the feed gas can become relatively depleted in trisilane as it traverses the substrate. As a result, greater amounts of film are deposited on the first-contacted portion of the substrate, where the local concentration of trisilane is relatively higher, than on the later-contacted portion of the substrate, where the local concentration of trisilane is relatively low. This effect is not typically observed when the feed gas is silane because silane deposition efficiency is relatively low as compared to trisilane.
It has been found that this problem may be addressed by adjusting the amount of trisilane supplied to the substrate surface, e.g., by increasing the flow rate of the feed gas, so that the rate at which trisilane is supplied to the surface is equal to or greater than the rate at which the trisilane is consumed by the deposition process. In practice, the flow rate of the feed gas is preferably selected in conjunction with the deposition temperature to provide the film with a greater degree of uniformity than a comparable film made using silane in place of trisilane, as illustrated in working Examples 16�19 below. Increasing the flow rate of trisilane is also advantageous because it allows for higher deposition rates. However, even when the trisilane flow rate is less than silane, all other conditions being equal, the deposition rate can be higher because of the greater deposition efficiency of trisilane, as illustrated in working Examples 5�15 below. Preferred flow rates thus may be adjusted to provide the desired degree of uniformity and the desired deposition rate, taking into account the deposition temperature and the partial pressure of trisilane in the feed gas, as well as practical considerations such as reactor size and configuration.
Dopant precursors include diborane, deuterated diborane, phosphine, and arsine. Silylphosphines [(H3Si)3-xPRx] and silylarsines [(H3Si)3-xAsRx] where x=0 �2 and Rx =H and/or D are preferred dopant sources of phosphorous and arsenic. SbH3 and trimethylindium are preferred sources of antimony and indium, respectively. Such dopants and dopant sources are useful for the preparation of preferred films such as boron-, phosphorous-, antimony-, indium-, and arsenic-doped silicon, SiGe and SiGeC films, by the methods described herein. The dopant concentration in these materials, when doped, is preferably in the range of from about 1�1014 to about 1�1022 atoms/cm3. Dopants can be incorporated using very low concentrations of the dopant sources, e.g., as mixtures in hydrogen with concentration ranging from about 1 ppm to about 1%, by weight based on total. These diluted mixtures can then be delivered to the reactor via a mass flow controller with set points ranging from 10 to 200 standard cubic centimeters per minute (sccm), depending on desired dopant concentration and dopant gas concentration. The dopant source is also preferably further diluted in the carrier gas delivered to the reactor with the silicon/germanium/carbon sources. Since flow rates often range from about 20 standard liters per minute (slm) to about 180 slm, the concentration of the dopant used in a typical process is usually very small.
For example, the effect of changing the amount of Ge precursor during CVD deposition using a silane-containing deposition gas is shown in FIGS. 5�8. During the illustrated depositions, the amount of Ge precursor (germane) in the deposition gas was varied by changing the germane flow rate. The effect of changing the germane flow rate on the amount of Ge incorporated into the film and on the deposition rate of the film was measured as described in the Examples below. At a deposition temperature of 600� C., FIG. 5 shows that the amount of germanium incorporated into the resulting film (left-hand axis) is not a linear function of the amount of germane in the deposition gas. Thus, a linear ramp-up or ramp-down in germane flow during deposition does not produce a Si�Ge film in which the Ge concentration has a correspondingly linear profile under these deposition conditions.
FIGS. 6�8 show that concentration and deposition rate non-linearities for thermal CVD using silane/germane are similarly observed at higher deposition temperatures. This means that the deposition problems encountered at 600� C. are not eliminated by increasing the deposition temperatures to 625� C. (FIG. 6), 650� C. (FIG. 7), or even 700� C. (FIG. 8). In fact, since the shapes of the plots are different at each temperature, these plots indicate that relatively small temperature variations across the surface of a substrate are likely to further complicate deposition using silane/germane.
The use of a deposition gas that contains trisilane greatly simplifies the task of depositing a graded Si-containing film using thermal CVD. For example, the effect of changing the amount of Ge precursor during CVD deposition using a trisilane-containing deposition gas is shown in FIGS. 9�10. The data shown in FIGS. 9�10 were obtained under the conditions described in the Examples below. In contrast to the non-linearities apparent in FIGS. 5�8, FIG. 9 shows that the Ge incorporation into the film is a substantially linear function of the germane flow rate. FIG. 9 also illustrates preferred linearity in the deposition rate as a function of the germane flow rate. The data is taken over a large range of Ge concentrations and Ge deposition rates of interest in IC fabrication contexts. It is preferred that both Ge incorporation and deposition rate be substantially linear functions of flow rate in order to facilitate the process of depositing graded Si�Ge films. Those skilled in the art will appreciate that data such as that shown in FIGS. 9 and 10 can be used to determine preferred conditions for the deposition of graded films, preferably graded Si�Ge films. FIG. 10 also illustrates preferred linearity of Ge incorporation and deposition rate for trisilane/germane under higher H2 flow rate conditions and a different germane concentration than illustrated in FIG. 9, demonstrating that the advantages of using trisilane are not limited to the specific conditions used to obtain the data in FIG. 9.
Preferably, polycrystalline SiGe-containing films, obtained by depositing over non-single crystal materials such as gate dielectric materials, have a surface roughness of about 10% or less, more preferably about 5% or less, based on the mean thickness of the film, as measured by atomic force microscopy on a 10 micron�10 micron scan area. When deposition is conducted as described herein, polycrystalline SiGe films can be obtained that have surface roughness values that are much less than comparable SiGe films deposited using silane in place of trisilane, as demonstrated in Examples 88�89 and FIGS. 12�15. Preferred amorphous SiGe-containing films are also very smooth, and preferably have a surface roughness of about 10% or less, more preferably about 5% or less, even more preferably about 2% or less, based on the mean thickness of the film, as measured by atomic force microscopy on a 10 micron�10 micron scan area.
Examples 1�4 Si-containing films were deposited using trisilane as a chemical precursor according to the parameters shown in Table 1. The deposition temperature was 700� C., well within the mass transport limited regime for trisilane. However, the resulting films were not uniform and instead had a concave deposition profile (thin in middle and thicker at edges) because the trisilane flow rate was inadequate (under these particular deposition conditions that were tuned for silane-based deposition) to provide a uniform film.
Examples 5�15 Si-containing amorphous films were deposited using trisilane and silane as chemical precursors and diborane as a dopant precursor according to the parameters shown in Table 1. About 120 sccm of 1% B2H6 in H2 was diluted in 2 slm H2 and 120 sccm of this mixture was introduced into the reactor where it was mixed with 20 slm H2 and trisilane or silane at the flow rate shown in Table 2. These results show that much higher deposition rates were generally obtained at a given temperature using trisilane, as compared to silane, even when the flow rate for trisilane was lower than that for silane.
Examples 16�19 Si-containing films were deposited using trisilane and silane as chemical precursors, according to the parameters shown in Table 3. Deposition times were adjusted so that the films each had an average thickness of about 500 Å. Deposition rates were determined by measuring average film thickness using a Nanometrics ellipsometer and then dividing this number by the deposition time. Film thickness non-uniformity was determined from a 49-point thickness map of the film thickness. The results show that a much more uniform film was obtained at a much higher deposition rate by using trisilane at the indicated temperature in place of silane. This is true at 550� C., but dramatically more so at 600� C.
Examples 20�38 Examples 1�19 are repeated except that SiGe films are obtained by using a mixture of 80% trisilane and 20% digermane in place of trisilane alone, and by using a mixture of 80% silane and 20% germane in place of silane. Higher deposition rates were observed than with the use of trisilane or silane alone.
Examples 40�48 (Comparative) A series of films was deposited using the ASM Epsilon 2000� horizontal flow epitaxial reactor system described above. Silane (20 sccm) and germane (1.5% in H2) were introduced into the reactor, mixed with 20 slm H2, and used to deposit a film onto a rotating substrate at a pressure of 80 torr and a temperature of 600� C., under the germane flow rate conditions shown in Table 4 below. The Ge concentrations in the resulting films were determined by Rutherford Backscattering Spectroscopy (RBS). Deposition rates were determined by measuring average film thickness using a Nanometrics ellipsometer and then dividing this number by the deposition time. The Ge concentration and deposition rate data are shown in Table 4 below and plotted in FIG. 5.
Ge in Film
Examples 49�57 (Comparative) A series of films was deposited under the conditions described above for Examples 40�48 under the flow rate conditions shown in Table 5 below, except that the deposition temperature was 625� C. The Ge concentrations in the resulting films and the deposition rates were determined as described above for Examples 40�48. The Ge concentration and deposition rate data are shown in Table 5 below and plotted in FIG. 6.
Examples 58�67 (Comparative) A series of films was deposited under the conditions described above for Examples 40�48 under the flow rate conditions shown in Table 6 below, except that the deposition temperature was 650� C. The Ge concentrations in the resulting films and the deposition rates were determined as described above for Examples 40�48. The Ge concentration and deposition rate data are shown in Table 6 below and plotted in FIG. 7.
Examples 68�76 (Comparative) A series of films was deposited under the conditions described above for Examples 40�48 under the flow rate conditions shown in Table 7 below, except that the deposition temperature was 700� C. The Ge concentrations in the resulting films and the deposition rates were determined as described above for Examples 40�48. The Ge concentration and deposition rate data are shown in Table 7 below and plotted in FIG. 8.
Examples 77�80 A series of films was deposited under the conditions described above for Examples 40�48 under the flow rate conditions shown in Table 8 below, except that trisilane was used in place of silane, the pressure was 40 torr, and the germane concentration in the H2was 10%. Trisilane was supplied to the reactor via a H2 bubbler at a flow rate set point of 25 sccm. The Ge concentrations in the resulting films and the deposition rates were determined as described above for Examples 40�48. The Ge concentration and deposition rate data are shown in Table 8 below and plotted in FIG. 9.
In contrast to the non-linearities apparent in FIGS. 5�8, FIG. 9 shows that the amount of Ge incorporated into the film is a substantially linear function of the germane flow rate. FIG. 9 also shows that the deposition rate is a substantially linear function of the germane flow rate.
Examples 81�86 A series of films was deposited under the conditions described above for Examples 77�80 under the flow rate conditions shown in Table 9 below, except that the germane concentration in the H2 was 1.5% and the H2 flow rate was 30 slm. The Ge concentrations in the resulting films and the deposition rates were determined as described above for Examples 40�48. The Ge concentration and deposition rate data are shown in Table 9 below and plotted in FIG. 10.
Like FIG. 9, FIG. 10 also shows that the amount of Ge incorporated into the film and the deposition rate are both substantially linear functions of the germane flow rate. FIG. 10 demonstrates that this substantial linearity is not limited to the deposition conditions of Examples 77�80, but can also be achieved under other deposition conditions.
Examples 90�110 A series of Si-containing films were deposited onto a SiO2 substrate (without a nucleation layer) at a pressure of 40 torr using trisilane and germane. The trisilane flow rate was constant at 77 sccm (hydrogen carrier, bubbler) for the examples of Table 10. Germane flow (10% germane, 90% H2) and deposition temperature were varied as shown in Table 10. Germanium concentration (atomic %) and thickness of the resulting SiGe films were determined by RBS, and surface roughness was determined by atomic force microscopy (AFM). The results shown in Table 10 demonstrate that highly uniform films can be prepared over a range of temperatures and flow rate conditions, particularly over a large range of germane concentration. High deposition rates are achieved at relatively low temperatures without sacrificing uniformity.
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availableJPS57209810A Title not availableJPS61153277A Title not available* Cited by examinerNon-Patent CitationsReference1Ikoma et al., Growth of Si/3C-SiC/Si(100) hetrostructures by pulsed supersonic free jets, Applied Physics Letters, vol. 75, No. 25, pp. 3977-3979, Dec. 1999.2Olivares, J. et al.; "Solid-phase crystallization of amorphous SiGe films deposited by LPCVD on SiO2 and glass," Thin Solid Films 337 (1999) pp. 51-54.3Todd, Michael A. et al., "Deposition of Si 1-x Ge x Films for Gate Electrode Applications Using a Novel Approach," ICS13, The SiGe Conference; Santa Fe, NM, Mar. 2003.Referenced byCiting PatentFiling datePublication dateApplicantTitleUS7720342Oct 31, 2008May 18, 2010Hewlett-Packard Development Company, L.P.Optical device with a graded bandgap structure and methods of making and using the sameUS7989360Jan 7, 2008Aug 2, 2011Micron Technology, Inc.Semiconductor processing methods, and methods for forming silicon dioxideUS8282735Nov 26, 2008Oct 9, 2012Asm Genitech Korea Ltd.Atomic layer deposition apparatusUS8545940Aug 30, 2012Oct 1, 2013Asm Genitech Korea Ltd.Atomic layer deposition apparatusClassifications U.S. Classification438/47, 257/E21.131, 257/E21.102, 438/318, 427/255.7, 438/320, 257/19, 427/124, 438/312, 438/235, 257/E21.119, 257/E21.166, 257/E21.17, 257/E21.101International ClassificationH01L21/425, H01L21/337, H01L29/51, H01L21/469, C23C16/02, H01L21/00, H01L29/737, H01L21/20, H01L27/092, H01L21/822, H01L21/331, H01L21/28, H01L29/78, C23C18/00, H01L31/18, C23C16/42, H01L21/8238, H01L21/285, C23C16/24, H01L21/316, H01L31/20, H01L21/205, C30B25/02Cooperative ClassificationY10S438/933, Y02E10/547, H01L21/02592, H01L21/02579, H01L31/1804, H01L21/02422, H01L21/0251, H01L21/02667, H01L21/02576, H01L21/3185, H01L21/0262, H01L21/0245, H01L29/517, H01L21/28194, C23C16/24, C23C16/22, C23C16/56, C23C16/308, H01L21/02532, H01L21/28525, C23C16/36, H01L21/02529, H01L21/02598, H01L29/518, H01L29/66242, H01L21/32055, H01L21/2257, C30B25/02, H01L21/28556, H01L21/28044, H01L28/84, C30B29/06, H01L29/66181, H01L29/51, C23C16/325, H01L21/02595, Y02E10/546, H01L29/127, H01L31/202, C23C16/30, H01L21/0243, H01L21/28035, C23C16/345, H01L31/182, B82Y30/00, C23C16/0272, B82Y10/00European ClassificationB82Y30/00, B82Y10/00, H01L21/02K4C1A3, H01L21/02K4B1A3, H01L21/02K4A5S, H01L21/02K4A1K, C30B25/02, C30B29/06, H01L21/02K4C3C1, H01L21/02K4E3C, H01L21/02K4C3C2, H01L21/318B, H01L21/02K4C1A2, H01L21/3205N, H01L29/51M, H01L21/225A4F, H01L29/66M6T2H, H01L21/28E2B2P, C23C16/30E, C23C16/36, C23C16/34C, H01L29/66M6D6, H01L29/51, C23C16/32B, H01L29/12W4, C23C16/56, C23C16/24, H01L21/02K4C5M2, H01L21/28E2C2D, H01L21/02K4C5M1, C23C16/22, H01L21/02K4C5M3, H01L28/84, H01L21/28E2B2, C23C16/30, H01L21/02K4B5L7, H01L21/20C, C23C16/02H, H01L21/205B, H01L21/20B, H01L31/18C, H01L21/285B4H, H01L31/18C5, H01L31/20B, H01L21/205, H01L21/285B4BLegal EventsDateCodeEventDescriptionAug 11, 2010FPAYFee paymentYear of fee payment: 4May 6, 2005ASAssignmentOwner name: ASM AMERICA, INC., ARIZONAFree format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNOR:TODD, MICHAEL A.;REEL/FRAME:016552/0099Effective date: 20020422RotateOriginal ImageGoogle Home - Sitemap - USPTO Bulk Downloads - Privacy Policy - Terms of Service - About Google Patents - Send FeedbackData provided by IFI CLAIMS Patent Services©2012 Google