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Publication numberUS3914473 A
Publication typeGrant
Publication dateOct 21, 1975
Filing dateMar 12, 1973
Priority dateMay 26, 1971
Publication numberUS 3914473 A, US 3914473A, US-A-3914473, US3914473 A, US3914473A
InventorsThomas Eugene Hale
Original AssigneeGen Electric
Export CitationBiBTeX, EndNote, RefMan
External Links: USPTO, USPTO Assignment, Espacenet
Method of making a coated cemented carbide product
US 3914473 A
A high-strength, coated cemented carbide product comprising a cemented carbide substrate and a fully dense alpha aluminum oxide coating on the substrate. The coating has a thickness of from 1-20 microns and is firmly and adherently bonded to the cemented carbide substrate through a thin intermediate nonmetallic layer of an iron group metal aluminate. The coated product combines a wear resistance substantially as high as aluminum oxide cutting materials and a transverse rupture strength of at least 150,000 psi. The coated product is prepared by passing water vapor, hydrogen gas and an aluminum halide over the substrate at a temperature of from 900 DEG -1250 DEG C., the ratio of water vapor to hydrogen gas being between about 0.025 and 2.0.
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Description  (OCR text may contain errors)

[ Oct. 21, 1975 METHOD OF MAKING A COATED CEMENTED CARBIDE PRODUCT [75] Inventor: Thomas Eugene Hale, Warren,


[73] Assignee: General Electric Company,

1 Schenectady, NY.

[22] Filed: Mar. 12, 1973 [21] Appl. No.: 339,653

Related U.S. Application Data [62] Division of Ser. No. 147,240, May 26, 1971, Pat. No.

[52] U.S. Cl. 427/255; 30/345 [51] Int. Cl. C23c 11/08 [58] Field of Search 117/106 R, 169 R; 29/1827; 423/625 [56] References Cited UNITED STATES PATENTS 3,251,337 5/1966 Latta et a1. 117/100 x 3,582,271 6/1971 Minagawa et al 423/625 3,736,107 5/1973 Hale 29/182.7

3,836,392 9/1974 Lux et a1 117/169 R OTHER PUBLICATIONS Powell et al., Vapor Deposition, John Wiley & Sons,

Inc, New York, 1966, pp. 384389.

Primary ExaminerRalph S. Kendall Assistant E.ruminerHarris A. Pitlick [5 7] ABSTRACT A high-strength, coated cemented carbide product comprising a cemented carbide substrate and a fully dense alpha aluminum oxide coating on the substrate. The coating has a thickness of from 1-20 microns and is firmly and adherently bonded to the cemented carbide substrate through a thin intermediate nonmetallic layer of an iron group metal aluminate. The coated product combines a wear resistance substantially as high as aluminum oxide cutting materials and a transverse rupture strength of at least 150,000 psi. The coated product is prepared by passing water vapor, hydrogen gas and an aluminum halide over the substrate at a temperature of from 900-1250C., the ratio of water vapor to hydrogen gas being between about 0.025 and 2.0.

3 Claims, No Drawings METHOD OF MAKING A COATED CEMENTED CARBIDE PRODUCT This application is a division of application Ser. No. 147,240, filed May 26," 1971, and now US. Pat. No. 3,736,107.

BACKGROUND OF THE INVENTION This invention relates to a high-strength, coated cemented carbide product and to a process for its preparation.

Cemented carbides are well known for their unique combination of hardness, strength and wear resistance and are accordingly extensively used for such industrial applications as cutting tools, drawing dies and wear parts. It is known that the wear resistance of cemented carbides may be enhanced by the application of a thin coating of a highly wear-resistant material, such as, for example, titanium carbide, and such coated cemented carbides are finding increasing commercial utility for certain cutting tool and machining applications. However, the increased wear resistance of such coated products has been at the sacrifice of the strength of the substrate which is substantially reduced after coating.

Because of its high hardness, wear resistance and low reactivity with a wide variety of metals, aluminum oxide has excellent potential as a tool material, and this potential has to some extent been realized with a variety of aluminum oxide cutting materials that are commercially available. The principal drawback to the more widespread use of aluminum oxide tools is their low strength which rarely exceeds 100,000 psi, using the standard transverse rupture or bend test. This compares with a strength of from 200,000 to 300,000, or even more, .for cemented carbide cutting tools. The low strengthof aluminum oxide tools limits their use to cutting applications where the tool is not highly stressed, such as in finishing cuts. The low strength of aluminum oxide also precludes the use of such materials in certain types of insert shapes which encounter high stresses when locked in a toolholder.

It is an object of this invention to provide a hard, wear-resistant material which combines the extremely high wear resistance of aluminum oxide with the relativ'ely high strength and hardness of cemented carbide.

It is an additional object of this invention to improve the wear resistance of cemented carbides without substantially reducing their strength. It is still an additional object of this invention to provide a process for producing a firmly adherent, nonporous, dense coating of aluminum oxide on a cemented carbide substrate.

SUMMARY OF THE INVENTION The foregoing and other objects of this invention are achieved by the vapor deposition under carefully controlled conditions of an alpha aluminum oxide coating of from 1-20 microns thickness on a cemented carbide substrate. The product contains a cemented carbide substrate and a fully dense alpha aluminum oxide coating firmly andadherently bonded to the substrate. In addition, there is present a very thin, intermediate nonmetallic layer of cobalt-, iron-, or nickel aluminate, which acts to metallurgically bond the coating to the substrate. The coated product has a wear resistance substantially equivalent to aluminum oxide base cutting materials and a transverse rupture strength of at least 150,000, in most cases greater than 200,000 pounds/sq. inch. At very high cutting speeds, greater than about 1,500 surface ft./minute in some applications, possibly higher in others, the higher heat resistance of solid aluminum oxide may result in higher wear resistance. But in all cutting tests other than those above these levels, the wear resistance of the present coated products has proven to be substantially as high as aluminum oxide cutting materials While the broad range of coating thicknesses useful in the invention is from l-20 microns, most coating thicknesses are preferably less than 15 microns. As will be shown in more detail below, certain applications require even narrower ranges within these limits, e.g. l-3 microns has proven optimum for machining high temperature alloys and for milling applications; 6-12microns has proven optimum for steel machining.

The process of the invention comprises passing an aluminum halide, water vapor and hydrogen gas over the carbide substrate at a temperature of from 900-1250C., the ratio of water vapor to the hydrogen gas being maintained between about 0.025 and 2.0, and preferably between 0.05 and 0.20.

There have previously been references in the literature of attempts or suggestions to coat a variety of substrates with aluminum oxide. However, insofar as is known, the coating of a cemented carbide substrate with aluminum oxide to produce a fully-dense and adherent coating has never previously been disclosed. Nor has the unusual combination of properties exhibited by the present products been previously attainable in either coated or uncoated cutting tool materials. The products of the invention are remarkable in several respects. Their strength as compared with comparable known coated cemented carbide materials is considerably higher and their cutting performance is superior in terms of tool life at intermediate and higher cutting speeds. The basis for the foregoing statements will become apparent from the discussion and test results set forth below.

The term cemented carbide as used herein means one or more transitional carbides of a metal of Groups IVb, Vb, and VIb of the Periodic Table cemented or bonded by one or more matrix metals selected from the group iron, nickel and cobalt. A typical cemented carbide contains WC in a cobalt matrix or TiC in a nickel matrix.

Because of the demanding requirements normally placed upon a cemented carbide cutting material, the properties of any coating, the manner in which it is bonded to the substrate and its effect on substrate strength are extremely critical. The coating layer must have high integrity in terms of density and smoothness porosity or nonuniformity cannot be tolerated. The coating must also be firmly and adherently bonded to the cemented carbide substrate to prevent spalling or separation in use. In addition, the coating must not reduce the strength of the cemented carbide substrate significantly. The products of the present invention have been extensively tested and have been found to satisfy all of the foregoing requirements. The coatings are uniform and fully dense, they are firmly bonded to the substrate and the coated composite retains a high proportion of its strength, usually greater than of the transverse rupture strength of the uncoated substrate. The achievement of these characteristics in the coated product is believed to be quite unexpected, particularly in view of the substantial strength reductions known to result from the addition of wear-resistant coatings to cemented carbide substrates. The coated materials of the invention also produce a surface finish in machining operations which appears to be fully equivalent in quality to solid aluminum oxide cutting materials, the latter being known to produce the best surface finishes.

, DESCRIPTION OF THE PREFERRED EMBODIMENTS The outstanding properties of the aluminum oxidecoated product of the invention depend upon careful control of the process parameters. The process involves the use of a gaseous mixture of hydrogen, water, and an aluminum halide such as aluminum trichloride. Carbon monoxide and carbon dioxide may be optionally added.

The primary overall deposition reaction is:

3H2O 2AlC| AIZOJ 6HCl.

The most important ingredients in the gaseous reaction mixture are therefore water vapor and aluminum chloride vapor. However, the aluminum chloride vapor can be formed in several ways during the deposition reaction, as for example by heating solid AlCl powder or by passing chlorine gas over aluminum metal. The water vapor is more conveniently formed by reacting hydrogen with carbon dioxide in the deposition chamber to form carbon monoxide and water vapor by the water gas reaction:

H; C02 CO +H,O

The amount of water vapor formed in this manner depends upon the temperature and the initial concentrations of hydrogen, carbon dioxide, carbon monoxide and water vapor in the input gas stream. In order to form a good quality coating of desirable thickness in the temperature range of 900-1250C., the ratio of water to hydrogen gases present, after the water gas reaction, should be between about 0.025 and 2.0.

Hydrogen has been found to be necessary in the vapor deposition process to obtain a dense, adherent coating. Hydrogen appears to insure oxidation of the aluminum at the carbide surface. Oxidation in the reaction zone above the carbide substrate creates a condition known as dusting which must be avoided. The absence of hydrogen creates a porous coating which is not fully dense. Thus the three necessary ingredients of the process are aluminum halide vapor, water vapor where a l K; K the equilibrium constant for the water gas reaction; [2 (CO),- (H2O),- K((H 2)i+ 2 )i); and 9 at-+0 2),- 2 )i 2 )i 2)i z h l- The parentheses denote the concentration of the gaseous species enclosed within in terms of partial pressure, and the subscripts (b) and (i) denote the final or equilibrium concentrations and the initial or input concentrations, respectively. The amount of H present, and thus the H O/H ratio, can then be determined from the relationship:

A series of coated products were prepared in accordance with the invention by passing aluminum chloride vapor, hydrogren and carbon dioxide over cemented carbide inserts. The examples were prepared at various input gas compositions and at various final H O/H concentrations. In all cases, deposition was at l050C. and a -minute deposition cycle was used with 2-3 grams of aluminum chloride and an aluminum chloride generator temperature of about 200C. The use of more AlCl shifts the desired H O/H ratio to a higher value and vice versa. The coatings were deposited on a cemented carbide substrate having the following composition in by weight: WG-72, Co-8.5, TiC-8, TaC-I 1.5. Table I below shows the effect of gas composition on coating thickness. When coating with both higher and lower ratios of H O/H (i.e. outside range of about 0.025 to 2.0), it wasnt possible to get a coating of sufficient thickness, i.e., 1 micron. Coating quality was good for all examples having more than 1 micron thickness coating. Coating quality was judged to be good if the coating could withstand an adherency test consisting of sliding the coated insert under a diamond brale indentor of the same type used for the Rockwell hardnes test using a load of 2 kilograms on the diamond. If the coating resisted spalling or crumbling during this test, it was judged to have good quality. If it did not, it was judged to have poor quality.

TABLE I Water Gas Reaction Equilibrium Coating Input Gas Partial Pressures Partial Pressures (H O)+ Thickness Example (H (CO (CO) (H O) (H (H O)+ (1-1 (Microns) and hydrogen. In its preferred form, the process includes the use of aluminum chloride vapor, hydrogen and carbon dioxide, the latter reacting with H to form water vapor.

The amount of water vapor present, after the reaction of known inputconcentrations of H and CO and CO and H 0 if used, can be calculated using the following equation:

The nature of the coating obtained was determined by using X-ray diffraction analyses and optical microscopy. X-ray analyses showed the coating to be alpha A1 0 At the higher deposition temperatures (greater than 1150C), significant amounts of the compound W CO C began to form due to reaction of the substrate carbide with the coating atmosphere. Optical microscopy revealed a gray, translucent coating of Al O that was fully dense and well bonded to the substrate in those examples in which the coating quality was found to be good. A very thin (less than 1 micron) layer of another nonmetallic compound, cobalt aluminate (CoAlwas present between the A1 0 layer and the ce- 5 mented carbide substrate. The presence of this thin layer is necessary to achieve the proper bond strength between the coating and the substrate, that is, a bond strength sufficient to pass the adherency test set forth above. In those cases in which no observable intermediate nonmetallic layer was present, the coated inserts did not pass the above described adherency test. For this reason, a cobalt (iron, or nickel) aluminate inter- 10 available solid aluminum oxide base (89% A1 0 11% TiO) insert Examples 2022 and a Ti C coated cemented carbide insert all run under the same conditions is also shown in Table 11.

TABLE II Coating Cutting Time to Transverse Thickness Speed .010 Flank Crater Depth at Rupture Example Insert Type (Mlcrons) SFPM Wear (Min.) .010 Flank Wear Strength (PS1) 1 1 A1 0; Coating on Cemented Carbide 1 700 9 .003" 260,000 12 4 700 32 .002" 250,000 13 7 700 51 .001" 235,000 14 10 700 51 .008 210,000 15 '7 1500 4.2 min. to .0003" (at 235,000 a .004" wear .004 flank wear) 16 A1 0 Coating on Cemented Carbide 7 1000 17 .007 175,000 17 12 1000 26 .003 160,000 18 Uncoated Carbide 700 4 .004" 270,000 19 Uncoated Carbide 1000 5 .010" 230,000 20 Solid A1 0 700 51 .001" 90.000 21 1000 .002" 90,000 22 1500 4.5 min. to .0002 (at 90,000

.004 wear .004 flank wear) 23 TiC Coating on Cemented Carbide 5 700 18 .01 1'' 175,000 24 5 1000 4 .011 175,000

72% WC, 8% TiC, 11.571 TaCv 8.5% Co; 71% WC, 12.5% TiC, 12% TaC, 4.57: Co.

mediate layer is believed necessary to a good quality coating.

The preferred temperature range for deposition of the coating is 900C. to l250C. At lower temperatures, the deposition rate becomes very low and the coating is poorly bonded to the substrate. At higher temperatures, excessive reaction occurs between the coating atmosphere and the cemented carbide substrate, weakening the bond between the coating and the substrate and lowering the strength of the overall composite body.

The strength of the A1 0 coated cemented carbide composite was measured (as were all strength measurements disclosed herein), using a slightly modified standard transverse rupture test (ASTM No. B4066-63T), that included three roll loading and a span-to-thickness ratio of 3.5 to 1. Using a deposition temperature of lOC. and a cemented carbide substrate of the nature set forth in the first ten examples in Table I above, the average strength of bars having coating thicknesses of from 5-7 microns (the preferred thickness for this substrate in terms of wear resistance) was 241,000 psi. This represents only a slight reduction l 1%) from the 270,000 strength value obtained from the uncoated cemented carbide substrate.

In the following Table II, the metal cutting performance of coated inserts prepared in accordance with this invention is shown and compared with the corresponding performance of uncoated inserts. Examples 1 1 through 17 were /2 X /2 X 3/16 inch disposable cutting inserts, coated with A1 0 at 1050C. by the vapor deposition technique disclosed above for Examples 1 through 10. A range of coating thicknesses of from 1-l0 microns was used. These inserts were then used 3 5 It can be seen that the cutting performance of the cemented carbide tool material is very substantially improved by the A1 0 coating and that this improvement is substantially greater than a TiC coating on the same substrate. It is also evident that the amount of improve- 40 ment obtained is dependent upon coating thickness up to a value of about 7 microns and that some evidence of performance decline occurs at 10 microns. At the optimum thickness value of 7 microns for this substrate, the performance of the A1 0 coated tool was 45 equivalent to that of the solid A1 0 tool at all three speeds tested. The strength of the A1 0 coated inserts was, however, considerably higher than solid A1 0 and higher than the strength of the same substrate with a TiC coating.

It should be noted that, because of strength limitations, it has not been feasible to use solid aluminum oxide cutting materials in disposable cutting inserts of the type used in pin-type holders. These inserts have a centrally disposed hole for the reception of a pin which locks the insert in place. The strength of such inserts must be sufficient to resist the locking stresses. The strength of the present coated materials is sufficiently high to enable their use in such inserts. The present invention therefore makes possible the use of an insert, in such applications, having a higher wear resistance than any comparable insert presently available.

The following Table III shows the performance of the coated inserts of the invention irtcutting a high tempersults, Example 25, are compared with the perfo gm of an uncoated cemented carbide of the same compo i;

TABLE III ments of the invention, and it is applicants intention in the appended claims to cover all forms which fall within the scope of the invention.

I claim:

1. A process of coating a cemented carbide substrate with a fully dense alpha aluminum oxide coating of from 1 microns thickness comprising contacting the carbide substrate with (passing an) Coating Thickness Time to .020"

Example Insert Type (Microns) Flank Wear (Min.) Comments A1 0 Coating on Cemented Carbide 2.5 8.5 26 Uncoated Cemented Carbide 5.4 27 Solid A1 0 l. Rapid edge breakdown.

The performance of the insert coated with 2.5 microns of A1 0 was significantly better than that of the uncoated cemented carbide insert of the same substrate composition. From tests with other coating thicknesses, it has been determined that-the optimum thickness for this kind of machining (i.e., high temperature alloys) is in the 1-3 micron range. Thicknesses greater than 3 microns in these tests decreased tool life. The superior strength of the A1 0 coated tools is amply demonstrated by the rapid failure of the solid Al O tool in Example 27, whereas no breakage or chipping was observed in the Al O coated tools, Example 25.

The foregoing is a description of illustrative embodi-

Patent Citations
Cited PatentFiling datePublication dateApplicantTitle
US3251337 *Jul 16, 1963May 17, 1966Earl S FunstonSpiral fluidized bed device and method for coating particles
US3582271 *Jul 11, 1968Jun 1, 1971Hitachi LtdMethod for manufacturing alumina whiskers
US3736107 *May 26, 1971May 29, 1973Gen ElectricCoated cemented carbide product
US3836392 *Jul 5, 1972Sep 17, 1974Sandvik AbProcess for increasing the resistance to wear of the surface of hard metal cemented carbide parts subject to wear
Referenced by
Citing PatentFiling datePublication dateApplicantTitle
US3967035 *May 15, 1975Jun 29, 1976General Electric CompanyCoated cemented carbide product
US4050951 *Dec 5, 1975Sep 27, 1977Societa' Italiana Resine S.I.R. S.P.A.Process for the post-treatment of titanium dioxide pigments
US4105443 *Jan 25, 1977Aug 8, 1978United Kingdom Atomic Energy AuthorityMetal-forming dies
US4112148 *May 26, 1977Sep 5, 1978Materials Technology CorporationMethod of co-deposit coating aluminum oxide and titanium oxide
US4336305 *Dec 13, 1979Jun 22, 1982Ngk Spark Plug Co., Ltd.Ceramic throw-away tips and process for producing the same
US4399168 *Jun 29, 1981Aug 16, 1983Santrade Ltd.Method of preparing coated cemented carbide product
US4406667 *May 20, 1982Sep 27, 1983Gte Laboratories IncorporatedNitride coated composite silicon nitride cutting tools
US4406668 *May 20, 1982Sep 27, 1983Gte Laboratories IncorporatedNitride coated silicon nitride cutting tools
US4409003 *May 20, 1982Oct 11, 1983Gte Laboratories IncorporatedCarbonitride coated silicon nitride cutting tools
US4409004 *May 20, 1982Oct 11, 1983Gte Laboratories IncorporatedCarbonitride coated composite silicon nitride cutting tools
US4421525 *May 20, 1982Dec 20, 1983Gte Laboratories IncorporatedAlumina coated composite silicon nitride cutting tools
US4440547 *May 20, 1982Apr 3, 1984Gte Laboratories IncorporatedAlumina coated silicon nitride cutting tools
US4449989 *Sep 26, 1983May 22, 1984Gte Laboratories IncorporatedCoated silicon nitride cutting tools
US4525415 *Sep 8, 1982Jun 25, 1985Iscar LimitedSintered hard metal products having a multi-layer wear-resistant coating
US4619866 *Apr 2, 1985Oct 28, 1986Santrade LimitedMethod of making a coated cemented carbide body and resulting body
US4696352 *Mar 17, 1986Sep 29, 1987Gte Laboratories IncorporatedInsert for a drilling tool bit and a method of drilling therewith
US4745010 *Jan 20, 1987May 17, 1988Gte Laboratories IncorporatedProcess for depositing a composite ceramic coating on a cemented carbide substrate
US4749629 *Jan 20, 1987Jun 7, 1988Gte LaboratoriesUltrathin laminated oxide coatings and methods
US4751109 *Jan 20, 1987Jun 14, 1988Gte Laboratories IncorporatedA process for depositing a composite ceramic coating on a hard ceramic substrate
US4880755 *Apr 3, 1989Nov 14, 1989Kennametal Inc.Sialon cutting tool composition
US4892792 *Aug 12, 1988Jan 9, 1990Gte Laboratories IncorporatedA1N coated silicon nitride based cutting tools
US4913936 *Mar 30, 1989Apr 3, 1990Kennametal Inc.Method of surface alloying sialon articles
US4943450 *Dec 14, 1989Jul 24, 1990Gte Laboratories IncorporatedMethod for depositing nitride-based composite coatings by CVD
US4950558 *Sep 23, 1988Aug 21, 1990Gte Laboratories IncorporatedOxidation resistant high temperature thermal cycling resistant coatings on silicon-based substrates and process for the production thereof
US4961780 *Mar 6, 1989Oct 9, 1990Vermont American CorporationBoron-treated hard metal
US4965140 *Jun 14, 1988Oct 23, 1990Gte Laboratories IncorporatedComposite coatings on refractory substrates
US5116416 *Oct 9, 1990May 26, 1992Vermont American CorporationBoron-treated hard metal
US5487625 *Nov 30, 1993Jan 30, 1996Sandvik AbOxide coated cutting tool
US5654035 *Sep 22, 1995Aug 5, 1997Sandvik AbMethod of coating a body with an α-alumina coating
US5693417 *May 22, 1995Dec 2, 1997Fraunhofer-Gesellschaft Zur Forderung Der Angewandten Forschung E.V.Vacuum-coated compound body and process for its production
US6447896May 5, 1986Sep 10, 2002Greenleaf Technology CorporationCoated reinforced ceramic cutting tools
US7531214 *Sep 28, 2006May 12, 2009Sandvik Intellectual Property AktiebolagMethod for manufacturing an oxide coated cutting tool
US20070020393 *Sep 28, 2006Jan 25, 2007Sandvik Intellectual Property Ab.Oxide coated cutting tool
USRE32093 *Apr 9, 1984Mar 18, 1986General Electric CompanyAluminum oxide coated titanium-containing cemented carbide product
USRE44870Aug 8, 2008Apr 29, 2014Sandvik Intellectual Property AbAluminum oxide coated cutting tool and method of manufacturing thereof
DE3211047A1 *Mar 25, 1982Nov 25, 1982Kennametal IncVorzugsweise mit bindemittel angereicherte, zementierte carbidkoerper und verfahren zu ihrer herstellung
DE3211047C2 *Mar 25, 1982Feb 11, 1988Kennametal Inc., Latrobe, Pa., UsTitle not available
WO1985001465A1 *Jul 19, 1984Apr 11, 1985Gte Laboratories IncCoated silicon nitride cutting tools
U.S. Classification427/255.19, 30/345
International ClassificationC23C16/40, C22C29/00, C23C30/00
Cooperative ClassificationC22C29/00, C23C16/403, C23C30/005
European ClassificationC22C29/00, C23C16/40D, C23C30/00B
Legal Events
Oct 30, 1987ASAssignment
Owner name: CARBOLOY INC., A DE. CORP.
Effective date: 19870925