|Numéro de publication||US3736107 A|
|Type de publication||Octroi|
|Date de publication||29 mai 1973|
|Date de dépôt||26 mai 1971|
|Date de priorité||26 mai 1971|
|Numéro de publication||US 3736107 A, US 3736107A, US-A-3736107, US3736107 A, US3736107A|
|Inventeurs||T E Hale|
|Cessionnaire d'origine||Gen Electric|
|Exporter la citation||BiBTeX, EndNote, RefMan|
|Référencé par (38), Classifications (16), Événements juridiques (1)|
|Liens externes: USPTO, Cession USPTO, Espacenet|
United States Patent 3,736,107 COATED CEMENTED CARBIDE PRODUCT Thomas E. Hale, Warren, Mich., assignor to General Electric Company No Drawing. Filed May 26, 1971, Ser. No. 147,240 Int. Cl. B22f 7/00 US. Cl. 29--182.7 9 Claims ABSTRACT OF THE DISCLOSURE 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 p.s.i. The coated product is prepared by passing water vapor, hydrogen gas and an aluminum halide over the substrate at a temperature of from 900-1250 C., the ratio of water vapor to hydrogen gas being between about 0.025 and 2.0.
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 in their low strength which rarely exceeds 100,000 p.s.i., using the standard transverse rupture or bend test. This compareswith a strength of from 200,000 to 300,000, or even more, for cemented carbide cutting tools. The low strength of 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, wearresistant material which combines the extremely high wear resistance of aluminum oxide with the relatively 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 con:
trolled 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 and adherently 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. 1-3 microns has proven optimum for machining high temperature alloys and for milling applications; 6-12 microns 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 900-1250 C., 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 IV b,
- 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 contain-s 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 itsstrength, 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:
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 most 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 +CO =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 900l250 C., 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 where a=1-K; K=the equilibrium constant for the water gas reaction; )1( 2 )1+ 2)1+( 2)1+ 2 )1) 2)1( 2)l+( 2)i( 2 )i 2 )l( 2)i+( 2 )l The parentheses denote the concentration of the gaseous species enclosed within in terms of partial pressure, and the subscripts f and 1' denote the final or equilibrium concentrations and the initial or input concentrations, respec tively. 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, hydrogen and carbon dioxide over cemented carbide inserts. The examples were prepared at various input gas compositions and at various final Hzo/Hg concentrations. In all cases, deposition was at 1050" C. and a minute deposition cycle was used with 2-3 grams of aluminum chloride and an aluminum chloride generator temperature of about 200 C. 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 percent by weight: WG-72, Co-8.5, TiC-S, TaC-11.5. Table I be low 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 suflicient 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 hardness 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 Input gas partial pressures partial pressures (Hz0)+ t1golatlng c ness z) (C 2) (C (H2O) (H2)+ (H2O)+ (H2)+ (microns 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 dustingwhich 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 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 input concentrations 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 difiraction analyses and optical microscopy. X-ray analyses showed the coating to be alpha A1 0 At the higher deposition temperatures (greater than 1150 C.), 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 A1 0 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, cob-alt aluminate (CoAl O was present between the A1 0 layer and the cemented carbide substrate. The presence of this thin layer is necessary to achieve the prop er bond strength between the coating and the substrate, that is, a bond strength sufiicient 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 intermediate layer is believed necessary to a good quality coating.
The preferred temperature range for deposition of the coating is 900 C. to 1250 C. At lower temperatures,
It can be'seen that the cutting performance of the cemented carbide tool material is very substantially improved by the Al O coating and that this improvement is substantially greater than a TiC coating on the same substrate. It is also evident that the amount of improvement the deposition rate becomes very low and the coating is 5 obtained is dependent upon coating thickness up to a value poorly bonded to the substrate. At higher temperatures, of about 7 microns and that some evidence of performance excessive reaction occurs between the coating atmosphere decline occurs at 10 microns. At the optimum thickness and the cemented carbide substrate, weakening the bond value of 7 microns for this substrate, the performance of between the coating and the substrate and lowering the 10 the A1 0 coated tool was equivalent to that of the solid strength of the overall composite body. A1 0 tool at all three speeds tested. The strength of the The strength of the A1 0 coated cemented carbide A1 0 coated inserts was, however, considerably higher composite was measured (as were all strength measurethan solid A12 3 and higher than the Strength of the Same ments disclosed herein), using a slightly modified standard substrate with a TiC coating. transverse rupture test (ASTM No. B4066-63T), that in- 15 It should be noted that, because of strength limitations, cluded three roll loading and a span-to-thickness ratio of it has not been feasible to use solid aluminum oxide cut- 3.5 to 1. Using a deposition temperature of 1050 C. ting materials in disposable cutting inserts of the type used and a cemented carbide substrate of the nature set forth in pin-type holders. These inserts have a centrally disin the first ten examples in Table I above, the average posed hole for the reception of a pin which locks the instrength of bars having coating thicknesses of from 5-7 56ft ill p The Strength of Such inserts must e ufmicrons (the preferred thickness for this substrate in terms ficient to resist the locking stresses. The strength of the f r e i t wa 241,000 p.s.i, Thi represents only present coated materials is sufiiciently high to enable their a slight reduction (11%) from the 270,000 strength value use in such inserts. The present invention therefore makes obtained from the uncoated cemented carbide substrate. possible the use of an insert, in such applications, having In the following Table II, the metal cutting performa higher wear resistance than any comparable insert presance of coated inserts prepared in accordance with this ently available. invention is shown and compared with the corresponding The following Table III shows the performance of the performance of uncoated inserts. Examples 11 through 17 Coated inserts of the invention in cutting a high temperawere X X disposable cutting inserts, coated ture nickel-base alloy, specifically Inconel 718 in the soluwith A1 0 at 1050 C. by the vapor deposition technique tion-aged condition (B'HN 390 hardness). The results, disclosed above for Examples 1 through 10. A range of EXample 25, are compared With the Performance f a coating thicknesses of from 1-10 microns was used. These uncoated cemented carbide of the same composition (Exinserts were then used to machine SAE 1045 steel, 190 ample 26), and in addition with a commercial solid BHN hardness, at 700-1000- and ISOO-surface-feet-peraluminum oxide tool (Example 27). The inserts were of minute speeds, .010 inch per revolution feed, and .100 the negative-rake disposable type (indexable and invertiinch depth of cut. The cutting times to a flank wear of ble) and were /2" x /2." x The cemented carbide .010 inch are shown in Table II, along with the crater wear substrate for Examples 25 and 26 was 94% WC and 6% depth at the .010 flank wear time. The transverse rupture Co. The substrate was coated with A1 0 at 1050 C. by strengths are also given. For comparison purposes, the vapor deposition process described above in connection cutting performance and strengths of the uncoated sub with Examples 1 through 10.
TABLE III Coating Time to thickness .020" flank Example Insert type (microns) Wear (min) Comments 25 A1203 coating on cemented carbide. 2. 5 8. 5 26.-. Uncoated cemented carbide 5. 4 27 Solid A1203- 1 Rapid edge breakdown.
strate material, Examples 18 and 19, a commercially available solid aluminum oxide base (89% Al O 11% TiO) insert-Examples 20-22and a TiC coated cemented car- The performance of the insert coated with 2.5 microns of Al O was significantly better than that of the uncoated cemented carbide insert of the same substrate bide insert-all run under the same conditions-is also composition. From tests with other coating thicknesses,
shown in Table II.
it has been determined that the optimum thickness for TABLE II Quotin Cutting Time to Crater depth Transverse thickness speed, .010 flank at .010 rupture strength Example (microns) s.i.p.m. wear (min.) flank wear (p.s.i.)
11 A coating on cemented carbide 1 700 9 003" 260, 000 d0. 4 700 32 .002 250,000 7 700 51 001 235, 000 10 700 51. 008" 210, 000 7 1,500 i 4. 2 0003" 235,000 7 1, 000 17 007" 175, 000 12 1, 000 26 003" 160,000 700 4 004" 270, 000 .60.. 1, 000 5 010" 230, 000 Solid Alto 700 51 .001 90,000 2l do 1, 000 30 002" 90, 000 22 1, 500 i 4. 5 0002" 90, 000 23... TiC coating on cemented carbide 5 700 18 011" 175, 000 2A -do. 5 1, 000 4 011 175, 000
1 72% W0, 8% TiC, 11.5% TaC, 8.5% Co. 9 To .004" wear.
a At .004" flank wear.
4 71% W0, 12.5% T10, 12% 'IaC, 4.5% Go.
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 coated tools is amply demonstrated by the rapid falure of the solid A1 0 tool in Example 27, whereas no breakage or chipping was observed in the A1 0 coated tools, Examples 25.
The foregoing is a description of illustrative embodiments 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 high-strength, high-wear-resistance coated cemented carbide product comprising a. cemented carbide substrate and a fully dense alpha aluminum oxide coating of from 1-20 microns thickness firmly and adherently bonded to said cemented carbide substrate through an intermediate layer of an iron group metal aluminate,
said coated cemented carbide product having a wear resistance substantially equivalent to aluminum oxide base cutting materials and having a transverse rupture strength of at least 150,000 p.s.i.
2. The coated cemented carbide product of claim 1 in which the cemented carbide substrate comprises tungsten carbide and a cobalt matrix.
3. The coated cemented carbide product of claim 2 in which the intermediate layer is cobalt aluminate.
4. The coated cemented carbide product of claim 1 in the form of a disposable cutting insert for the machining of metal and other materials.
5. The coated cemented carbide insert of claim 4 having a centrally disposed hole therein, the insert adapted to be mounted in a pin-type toolholder.
6. The coated cemented carbide product of claim 1 in which the coating is less than 15 microns in thickness.
7. The coated cemented carbide product of claim 1 in which the cemented carbide substrate comprises titanium carbide and a matrix selected from the group consisting of iron, nickel and cobalt.
8. The coated cemented carbide product of claim 7 containing tantalum carbide.
9. The coated cemented carbide product of claim 1 in which the cemented carbide substrate comprises tungsten carbide, titanium carbide and tantalum carbide and a cobalt matrix.
References Cited UNITED STATES PATENTS 3,565,643 2/1971 Bergna 10643 3,110,571 11/1963 Alexander et a1. 10665 FOREIGN PATENTS 819,086 8/1959 Great Britain 29182.2
CARL D. QUARFORTH, Primary Examiner US. Cl. X.R.
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|Classification aux États-Unis||428/131, 75/236, 419/5, 428/332, 75/235, 75/242, 428/698, 428/701|
|Classification internationale||C22C29/00, B23B27/14, B22F3/24, C23C16/30|
|Classification coopérative||C23C16/403, C22C29/00|
|Classification européenne||C23C16/40D, C22C29/00|
|23 avr. 1985||RF||Reissue application filed|
Effective date: 19840419