Patent Grant
6866921
The invention pertains to a chromium-containing cemented carbide body (e.g., a coated cemented (cobalt-chromium binder alloy) tungsten carbide cutting insert) that has a surface zone of binder alloy enrichment.
Coated cemented carbide (e.g., cemented [cobalt] tungsten carbide) cutting inserts that exhibit a surface zone of binder enrichment are in use for metal cutting applications. The surface zone of binder enrichment may be stratified such as shown in the article “The Microstructural Features and Cutting Performance of the High Edge Strength Kennametal Grade KC850”, Proceedings of the Tenth Plansee Seminar, Reutte, Trol, Austria, Metalwerke Plansee A. G. (1981), pp. 613-627. The surface zone of binder enrichment may be non-stratified such as shown in U.S. Reissue Pat. No. 34,180 to Nemeth et al. or U.S. Pat. No. 5,955,186 to Grab.
Current coated cemented carbide cutting inserts that exhibit a surface zone of binder enrichment have acceptable performance characteristics. However, it would still be desirable to provide a coated cemented carbide cutting insert that has improved performance characteristics.
In one form thereof, the invention is a cutting insert having a tungsten carbide based bulk composition of at least 70 weight percent tungsten and carbon, between about 3 weight percent and about 12 weight percent cobalt, and at least 0.09 weight percent chromium. The cobalt and chromium form a binder alloy. The binder alloy content of the composition is enriched in a surface zone beginning near and extending inwardly from the peripheral surface of the substrate.
The substrate also preferably contains nitrogen as a result of the mechanism used to obtain binder enrichment.
Preferably, the tungsten carbide based bulk composition has up to about 10 weight percent tantalum, up to about 6 weight percent niobium, and up to about 10 weight percent titanium.
Preferably, there is at least one weight percent total of tantalum, niobium, and titanium, and more preferably, at least two weight percent total of tantalum, niobium, and titanium.
Preferably, the ratio of the weight percent of chromium to the weight percent of cobalt ranges between about 0.03 to about 0.15, and more preferably, between about 0.05 to 0.10.
Preferably, the ratio of the weight percent of chromium to the weight percent cobalt remains about constant between the surface zone of binder alloy enrichment and the bulk composition.
Preferably, the cutting insert in accordance with the invention has a substrate composition as described above and a hard coating thereon composed of one or more layers. Preferably, the innermost layer contains chromium, which has diffused into the layer from the substrate during chemical vapor deposition of the coating onto the substrate, preferably forming a chromium containing solid solution layer (e.g., a titanium chromium carbonitride, or a titanium tungsten chromium carbonitride).
These and other aspects of the invention will become more clear upon review of the following detailed description of the invention in conjunction with the drawings.
The following is a brief description of the drawings that form a part of this patent application:
Referring to the drawings,
The coated cutting insert 10 further includes a substrate generally designated as 18 (se FIG. 2). The substrate 18 has a bulk region 20 and a surface zone of binder alloy enrichment 22 that has a maximum binder alloy content greater than the binder alloy content in the bulk region 20 of the substrate. The substrate 18 has a rake surface 24 and a flank surface 26. In this specific embodiment, the surface zone of binder alloy enrichment 22 extends inwardly from both the rake surface 24 and the flank surface 26 of the substrate 18 near the cutting edge 12. The surface zone of binder alloy enrichment is removed from the other areas of the cutting insert by grinding.
The substrate 18 comprises a cemented carbide material. One exemplary substrate is a cemented (cobalt-chromium binder alloy) tungsten carbide that contains one or more carbide forming elements such as, for example, titanium, tantalum, niobium, zirconium, and hafnium. The material may also contain vanadium, but the vanadium must be present along with one or more of the above-identified carbide-forming elements; namely, titanium, tantalum, niobium, zirconium, and hafnium. The substrate also contains chromium wherein most, if not all, of the chromium is alloyed with the cobalt to form a cobalt-chromium binder alloy. Other elements may optionally be a component of the binder alloy wherein these elements include tungsten, iron, nickel, ruthenium, and rhenium. In some instances, up to 20 weight percent of the binder alloy may comprise tungsten.
In the case of a cemented (cobalt-chromium binder alloy) tungsten carbide, the surface zone of binder alloy enrichment typically exhibits a non-stratified type of binder alloy enrichment. The porosity of the bulk substrate is typically Type A to Type B porosity according to ASTM Designation B276-91 (Reapproved 1996). Applicants consider that the scope of this invention also encompasses a substrate with a surface zone of non-stratified binder alloy enrichment wherein the bulk substrate has a Type C porosity according to ASTM Designation B276-91 (Reapproved 1996). U.S. Reissue Pat. No. 34,180 to Nemeth et al. discloses cemented tungsten carbide cutting inserts that exhibit the non-stratified type of binder enrichment. Pending U.S. patent application Ser. No. 09/534,710 filed on Mar. 24, 2000 and entitled Cemented Carbide Tool and Method of Making to Liu et al. discloses a substrate with a porosity rating according to ASTM Designation B276-91 (Reapproved 1996) of greater than C00, and a surface zone of non-stratified binder enrichment.
In addition, applicants consider that the scope of the invention encompasses a substrate with a surface zone of stratified binder alloy enrichment. The typical substrate with a surface zone of stratified binder alloy enrichment has a bulk substrate with a Type C porosity according to ASTM Designation B276-91 (Reapproved 1996). An example of a substrate with a Type C porosity and a surface zone of stratified binder alloy enrichment is in the above-mentioned article entitled “The Microstructural Features and Cutting Performance of the High Edge Strength Kennametal Grade KC850”. However, applicants still contemplate that the scope of the invention may encompass a substrate with a surface zone of stratified binder enrichment that has a bulk substrate with Type A and/or Type B porosity according to ASTM Designation B276-91 (Reapproved 1996). The article to Kobori et al. entitled “Binder Enriched Layer Formed Near the Surface of Cemented Carbide”, Funtai Oyobi Funtai Yakin, Vol. 34, No. 1, pages 129-132 (1987), describes the stratified type of binder enrichment.
A range for the components of an exemplary substrate made of cemented (cobalt-chromium binder alloy) tungsten carbide, i.e., a tungsten carbide-based material, comprises between about 3 weight percent to about 12 weight percent cobalt, up to about 10 weight percent tantalum, up to about 6 weight percent niobium, up to about 10 weight percent titanium, greater than about 70 weight percent tungsten and carbon, and a minimum of 0.09 weight percent of chromium. The upper limit on chromium content is determined by the level at which the substrate can still avoid toughness problems associated with the specific application in question. The preferably upper limit for chromium is about 15 percent of the cobalt content (e.g., 1.8 w/o chromium at 12 w/o cobalt; 0.45 w/o chromium at 3 w/o cobalt) or more preferably, 10 percent of the cobalt content (e.g., 1.2 w/o at 12 w/o cobalt; and 0.3 w/o chromium at 3 w/o cobalt). Preferably, the lower limit of chromium content is also dependent on cobalt content and should be at least 3 percent of the cobalt content (e.g., 0.09 w/o chromium at 3 w/o cobalt; and 0.36 w/o chromium at 12 w/o cobalt, and more preferably, at least 5 percent of the cobalt content (e.g., 0.15 w/o chromium at 3 w/o cobalt, and 0.6 w/o chromium at 12 w/o cobalt).
Another range for the components for an exemplary substrate made of cemented (cobalt-chromium binder alloy) tungsten carbide comprises between about 5 and about 6 weight percent cobalt, between about 3 and about 4 weight percent tantalum, between about 1 and about 2.5 weight percent titanium, between about 0.2 and about 0.6 weight percent niobium, chromium present in an amount between about 0.2 weight percent and about 0.4 weight, and at least about 70 weight percent tungsten and carbon.
Applicants contemplate that in an exemplary substrate the surface zone of binder alloy enrichment may extend inwardly from the peripheral surface of the substrate to a depth of up to about 50 micrometers. In another exemplary substrate, the range for the depth of binder alloy enrichment is between about 20 and about 30 micrometers.
In one exemplary substrate, the maximum binder alloy content in the surface zone of binder alloy enrichment ranges between about 125 and about 300 weight percent of the binder content in the bulk substrate. In another exemplary substrate, the maximum binder alloy content in the surface zone of binder alloy enrichment ranges between about 150 weight percent and about 300 weight percent of the binder alloy content in the bulk substrate. In still another exemplary substrate, the maximum binder alloy content in the surface zone of binder alloy enrichment ranges between about 200 and about 300 weight percent of the binder alloy content in the bulk substrate. In yet another exemplary substrate the binder alloy content in the surface zone of binder alloy enrichment ranges between about 150 and about 250 percent of the binder alloy content in the bulk substrate.
In one exemplary substrate that comprises cemented (cobalt-chromium binder alloy) tungsten carbide, a specific range for the physical properties is a hardness of between about 89 and about 93 Rockwell A, a coercive force (HC) of between about 115 and about 350 oersteds, and a magnetic saturation between about 128 [162 micro Tesla cubic meter per kilogram cobalt (μT-m3/kg)] and about 160 gauss cubic centimeter per gram cobalt (gauss-cm3/gm) [202 micro Tesla cubic meter per kilogram cobalt (μT-m3/kg)]. In another exemplary substrate that comprises cemented (cobalt) tungsten carbide, a specific range for the physical properties is a bulk hardness of between about 91.5 and about 92.5 Rockwell A, a coercive force (HC) of between about 155 and about 195 oersteds, and a magnetic saturation between about 128 gauss cubic centimeter [162 micro Tesla cubic meter per kilogram cobalt (μT-m3/kg)] and about 160 gauss cubic centimeter per gram cobalt (gauss-cm3/gm) [202 micro Tesla cubic meter per kilogram cobalt (μT-m3/kg)].
As shown in
As exemplary coating materials the base layer may comprise one or more materials selected from the group consisting of one or more of the carbides, nitrides, carbonitrides and oxides of titanium.
The intermediate layer may comprise one or more materials selected from the group consisting of titanium carbonitride, titanium nitride, titanium carbide, alumina, titanium aluminum nitride, zirconium nitride, zirconium carbide, hafnium nitride, and hafnium carbide.
The outer layer may comprise one or more materials selected from the group consisting of titanium carbonitride, titanium nitride, titanium carbide, alumina, titanium aluminum nitride, titanium diboride, chromium nitride, hafnium nitride, and hafnium carbide.
Generally speaking, one or more of the coating layers of the coating schemes are applied by chemical vapor deposition (CVD) and moderate temperature chemical vapor deposition (MTCVD). However, applicants also contemplate that one or more layers of a coating scheme may be applied by physical vapor deposition (PVD).
The substrate may contain a layer eta phase between the base coating layer and the substrate. The layer of eta phase is no thicker than between about 2 micrometers to about 3 micrometers.
A cutting insert typically used in turning applications generally presents a surface zone of binder alloy enrichment that extends inwardly from both the rake surface and the flank surface of the substrate. Such is the case for the cutting insert illustrated in
There are, however, certain cutting inserts used for certain applications in which the surface zone of binder alloy enrichment extends inwardly only from the rake surface of the substrate and any binder alloy enrichment is absent from the other surfaces of the substrate. In these styles of cutting inserts, the flank surface of the sintered substrate is typically ground to remove the surface zone of binder alloy enrichment that extends from the flank surface so as to leave the surface zone of binder alloy enrichment that extends from the rake surface.
Cutting insert 40 has substrate generally designated as 49 (see
The substrate 49 of cutting insert 40 may be essentially the same composition and present the same level of binder enrichment as the substrate 18 of cutting insert 10. Cutting insert 40 has a coating scheme shown in brackets 59 that may be the same as the coating scheme 29 of cutting insert 10. In this regard, coating scheme 59 presents a base layer 60, a mediate layer 62 on the base layer 60, and an outer layer 64 on the mediate layer 62. Additional description of the substrate 49 and the coating scheme 59 is not necessary.
Coated cutting inserts comprising Substrate No. 1 (as described hereinafter) and the coating scheme described as follows were subjected to an analysis via transmission electron microscopy (TEM). This coating scheme comprised: a base layer of titanium nitride applied to the substrate by CVD to a thickness of 0.5 micrometers, a first mediate layer of titanium carbonitride applied by MTCVD to the base layer to a thickness of 4 micrometers, a second mediate layer of alumina applied to the first mediate layer by CVD to a thickness of 1.5 micrometers, and an outer layer of titanium nitride applied to the second mediate layer by CVD to a thickness of 0.5 micrometers.
This TEM analysis revealed that the ratio of the weight percent chromium to the weight percent of cobalt (wt % chromium/wt % cobalt) was uniform between the surface zone of cobalt enrichment and the bulk substrate. The composition of the cobalt or binder alloy phase in the surface zone of enrichment was equal to 4.5 weight percent chromium and 95.5 weight percent cobalt (or 5 atomic percent chromium and 95 atomic percent cobalt). Since the weight percent ratio of the starting chromium and cobalt contents was 0.3 to 5.75, which is about 5 percent, it appeared that most, if not all, of the chromium was in the cobalt binder. Applicants would also expect that some tungsten would be in the binder alloy so that up to 20 weight percent of the binder alloy may comprise tungsten.
Even though the base layer comprises titanium nitride or titanium carbonitride, due to the higher temperature (i.e., 900 to 1000 degrees Centigrade) at which the base layer is applied, there is believed to be some diffusion of carbon from the substrate into the base layer so that the titanium nitride changes to titanium carbonitride or the carbon content of the titanium carbonitride increases. It was surprisingly discovered that some of the chromium in the substrate diffused into the base layer so that the base layer is believed to comprise a solid solution titanium-chromium carbonitride, or a solid solution titanium-tungsten-chromium carbonitride.
A TEM thin foil was analyzed for chemistry via a Philips CM200 Field Emission Gun TEM, using the EMi SPEC interface to the EDS system. The results of this analysis for the metals in the base coating layer is shown below:
Applicants believe that the diffusion of chromium into the base layer of the coating scheme improves the adhesion of the coating to the substrate and the wear resistance of the coating so as to improve the performance of the cutting insert. TEM analysis of the base coating layer adjacent to the substrate found that the ratio of the chromium to the cobalt in the base coating layer was about 1.9/2.3 on an atomic percent basis with chromium being present in the base layer at about 1.9 atomic percent. This is surprisingly a significantly higher chromium/cobalt ratio (0.83) than found in the substrate (approximately 0.05). The inventors believe that to maximize enhanced adhesion and wear resistance, the ratio of the Cr/Co ratio in the coating to the Cr/Co ratio in the substrate should preferably be greater than 5, more preferably, greater than 10, and most preferably, greater than 15.
Coated cutting inserts were made and tested in turning tests and slotted bar tests. Set forth below is a description of these cutting inserts and the test results.
Table 1 below presents the composition in weight percent of the elements that comprise the substrates. In the starting powder mixtures to make Substrates Nos. 1 and 2 nitrogen is present in the form of titanium nitride. In the starting powder mixture to make Substrates Nos. 3 and 4 nitrogen is present in the form of titanium carbonitride wherein the carbon to nitrogen ratio is 1:1. For the starting powder mixtures to make each one of the Substrates Nos. 1 through 4, the chromium is present in the form of chromium carbide.
The above substrates were prepared by conventional powder metallurgical sintering techniques including ball milling, pressing the powders into a green compact (i.e., a consolidated mass of the starting powders), delubing (or dewaxing) the green compact, and vacuum sintering. For these substrates, the vacuum sintering occurred at a temperature of about 2700 degrees Fahrenheit (1482 degrees Centigrade) for a duration of about 45 to about 90 minutes. Table 2 below sets forth some of the physical properties of the sintered substrates.
Table 2 presents the coercive force (HC) in oersteds (Oe), the magnetic saturation (MS) in gauss cubic centimeter per gram cobalt, the thickness of the surface zone of binder (cobalt) enrichment (CEZ) in micrometers, the hardness in Rockwell A of the bulk of the substrate, and the porosity of the bulk substrate as measured by ASTM Designation B 276-91 (Reapproved 1996) entitled “Standard Test Method for Apparent Porosity in Cemented Carbides”.
Substrates Nos. 1 and 2 were ground top and bottom and honed, and then were coated with the following coating scheme (Coating Scheme A): a base layer of titanium nitride applied by chemical vapor deposition (CVD) to a thickness of 0.5 micrometers, a first mediate layer of titanium carbonitride applied to the base layer by moderate temperature chemical vapor deposition (MTCVD) to a thickness of 3.5 micrometers, a second mediate layer of titanium carbonitride applied to the first mediate layer by CVD to a thickness of 0.5 micrometers, a third mediate layer of alumina (kappa phase) applied to the second mediate layer by CVD to a thickness of 2.0 micrometers, and an outer layer of titanium nitride applied by CVD to the third mediate layer to a thickness of 0.5 micrometers.
Table 3 below sets forth the results in tool life as measured in minutes of four repetitions of turning tests under the following parameters: a speed equal to 590 surface feet per minute [180 surface meters per minute], a feed equal to 0.010 inches per revolution (ipr) [0.25 millimeters per revolution], a depth of cut equal to 0.080 inches (2 millimeters), and flood coolant. The workpiece material was a 316Ti stainless steel bar (German DIN 1.4571). The style of the cutting insert was CNMG432 with a 6 degree positive rake.
The failure mode for each one of the cutting inserts used in the turning tests reported in Table 3 was depth of cut notching. The tool life criteria for the turning test tool life results presented in Table 3 were: uniform flank wear equal to 0.015 inches (0.38 millimeters); maximum flank wear equal to 0.030 inches (0.76 millimeters); nose wear equal to 0.03 inches (0.76 millimeters); depth of cut notching equal to 0.020 inches (0.51 millimeters); crater wear equal to 0.004 inches (0.10 millimeters); and trailing edge wear equal to 0.030 inches (0.76 millimeters).
Substrates Nos. 3 and 4 were coating according to the following scheme (Coating Scheme B): a base layer of titanium nitride applied to the substrate by CVD to a thickness of 0.5 micrometers, a first mediate layer of titanium carbonitride applied to the base layer by MTCVD to a thickness of 3.5 micrometers, a second mediate layer of titanium carbonitride applied to the first mediate layer by CVD to a thickness of 0.5 micrometers, a third mediate layer of alumina (kappa phase) applied to the second mediate layer by CVD to a thickness of 2.5 micrometers, and an outer layer of titanium nitride applied by CVD to the third mediate layer to a thickness of 0.5 micrometers. As described above, because of the temperature (i.e., 900 to 1000 degrees Centigrade) at which the base layer was applied, applicants expect that carbon and chromium each diffused into the base layer of the coating scheme so that the base layer comprised a titanium-chromium solid solution carbonitride where the carbon and chromium contributions were from the substrate.
Table 4 below sets forth the test results in tool life as measured in minutes of a slotted bar test done at the following parameters: a speed equal to 500 surface feet per minute (sfm) [152 surface meters per minute], a feed equal to 0.006 inches per revolution (ipr) [1.5 millimeters per revolution], and a depth of cut equal to 0.100 inches [2.5 millimeters], and flood coolant. The workpiece material was a 304 stainless steel bar (German DIN 1.4301). The style of the cutting insert was CNMG432 with a 6 degree positive rake.
The slotted bar had two diametrically opposed 0.75 inch maximum (1.91 centimeters) radial slots on a six inch diameter bar. For each one of the cutting inserts used in the slotted bar test results reported in Table 4, the failure mode was chipping or fracture of the cutting insert.
Substrates Nos. 3 and 4 were coated according to the following coating scheme (Coating Scheme C): a base layer of titanium carbonitride was applied to the substrate by CVD to a thickness of 2 micrometers, a mediate layer of titanium carbide was applied to the base layer by CVD to a thickness of 4 micrometers, and an outer layer of alumina was applied to the mediate layer by CVD to a thickness of 1.5 micrometers. These coated cutting inserts were then tested in the turning of 316Ti stainless steel under the following operating parameters: a speed equal to 590 sfm [180 smm], a feed equal to 0.010 ipr [0.25 mmpr], and a depth of cut equal to 0.080 inches [2.0 mm]. Table 5 sets forth the test results as tool life measured in minutes. The style of the cutting insert was CNMG432 with a 6 degree positive rake.
The failure mode for each one of the cutting inserts used in the turning tests reported in Table 5 was depth of cut notching. The tool life criteria for the turning test tool life results presented in Table 5 were: uniform flank wear equal to 0.015 inches (0.38 millimeters); maximum flank wear equal to 0.030 inches (0.76 millimeters); nose wear equal to 0.03 inches (0.76 millimeters); depth of cut notching equal to 0.020 inches (0.51 millimeters); crater wear equal to 0.004 inches (0.10 millimeters); and trailing edge wear equal to 0.030 inches (0.76 millimeters).
Cutting inserts (Style CNMG432 with a 6 degree positive rake) were also tested by a slotted bar test under the following parameters: a speed equal to 500 surface feet per minute (sfm) [152 surface meters per minute], a feed equal to 0.006 inches per revolution (ipr) [0.15 millimeters per revolution], and a depth of cut equal to 0.100 inches [2.5 millimeters], and in which the workpiece material was 304 stainless steel. Table 6 presents the test results as tool life measured in minutes.
For each one of the cutting inserts used in the slotted bar test results reported in Table 6, the failure mode was breakage of the cutting insert.
These test results show that for the overall turning of 316Ti stainless steel, the coated cutting inserts that had chromium in the substrate thereof had 181 percent longer tool life and a 157 percent longer tool life. More specifically, for the coated cutting inserts having the A coating scheme [Substrates Nos. 1 and 2], the cutting insert with the substrate containing chromium had 181 percent longer tool life than the cutting insert with the substrate that did not contain chromium. For the coated cutting inserts having the C coating scheme [Substrates Nos. 3 and 4], the cutting insert with the substrate containing chromium had 157 percent longer tool life than the cutting insert with the substrate that did not contain chromium.
These test results also show that for the slotted bar test, the coated cutting inserts that had chromium in the substrate thereof had 193 percent longer tool life and a 153 percent longer tool. More specifically, for the coated cutting inserts having the B coating scheme [Substrates Nos. 3 and 4], the cutting insert with the substrate containing chromium had 193 percent longer tool life than the cutting insert with the substrate that did not contain chromium. For the coated cutting inserts having the C coating scheme [Substrates Nos. 3 and 4], the cutting insert with the substrate containing chromium had 153 percent longer tool life than the cutting insert with the substrate that did not contain chromium.
Applicants believe that the improvement in the performance by the cutting inserts that contain chromium is due to the better adhesion of the coating to the substrate. Applicants believe that the better adhesion is principally due to the diffusion of the chromium into the base layer during the coating process. The presence of the chromium in the base layer is consistent with the improvement in the depth of cut notching.
All patents and documents identified in this patent application are hereby incorporated by reference herein.
Other embodiments of the invention will be apparent to those skilled in the art from a consideration of the specification or practice of the invention disclosed herein. Applicants intend that the specification and the examples are only illustrative, and that the claims define the true scope and spirit of the invention.
This application is a continuation of U.S. patent application Ser. No. 09/638,048, filed Aug. 11, 2000, now U.S. Pat. No. 6,554,548.
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| Number | Date | Country | |
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| Child | 10383792 | US |
