Low pressure bonding of PCD bodies and method for drill bits and the like

An improved temperature stable synthetic polycrystalline diamond (PCD) product includes at least one temperature stable PCD integrally and chemically bonded to a matrix carrier support through a carbide forming layer which is of a thickness of at least about 1 micron, the layer on at least one surface of the PCD is in turn bonded to the matrix carrier. A wide variety of shapes, sizes and configurations of such products is achieved through relatively low temperature and relatively low pressure processing. Various products of various geometries are described as well as the details of the processing to achieve chemical bonding of the PCD elements in a variety of support matrix carrier materials to form a unitary structure having a temperature stability up to about 1,200 degrees C.

FIELD OF INVENTION 
The present invention relates to an improved synthetic diamond product and 
method of making the same and more particularly to an improved and novel 
temperature stable diamond assembly which may be of a variety of sizes, 
shapes, and thickness, the diamond assembly being formed by an improved 
and novel bonding method which does not require the comparatively high 
temperatures and pressures normally used in the synthesis of synthetic 
diamond products thus to provide a diamond assembly which may be 
relatively large and in which the diamond, preferably in the form of a 
temperature stable synthetic polycrystalline diamond, is firmly and 
chemically bonded on or to a support structure. 
BACKGROUND OF THE INVENTION 
Various types of synthetic diamond products are known and commercially 
available. Typically such products are used industrially for material 
removal purposes, for example, drilling products such as core bits, mining 
bits, drilling bits for oil and gas, saw products, cutting tools, grinding 
wheels, and products such as wire-drawing and extruding dies, bearing 
surfaces, dressers, lead bonding tools and abrasives. 
These synthetic diamond materials may vary somewhat in their character, one 
being an unleached polycrystalline product having a temperature stability 
of up to about 700-750 degrees C., see U.S. Pat. Nos. 3,745,623 and 
3,609,818. This synthetic diamond product itself is usually formed by 
diamond-to-diamond bonds and is carried on a substrate which may be 
cemented tungsten carbide, for example. The substrate is usually preformed 
and contains cobalt, the diamond product being formed and affixed to the 
substrate at very high temperatures and pressures, usually referred to as 
the diamond stable region of temperature and pressure, as set forth in 
prior patents and other literature, and typically above 50 kbar and at a 
temperature above about 1,200 degrees C. 
These products are often referred to as polycrystalline diamond products 
(PCD) as contrasted to single crystal diamonds. PCD elements offer the 
advantage that upon fracture, only a relatively small fragment of the PCD 
element is lost as compared to a single crystal diamond in which fracture 
takes place along a plane with the possibility of losing a relatively 
large piece of the diamond. 
Unleached PCD elements may be formed with the high temperature and high 
pressure apparatus as disclosed, for example, in U.S. Pat. No. 2,941,248. 
PCD products thus far described are available in various sizes and shapes, 
for example circular, half-circles, quarter round, square, rectangular, 
half-rounds with a pointed section, and the like. The PCD face or disc, 
joined to a backing member of tungsten carbide or the like is sometimes 
mounted, by brazing, on a steel tool body or tungsten carbide slug 
support. The PCD materials may be as small as several millimeters to as 
large as 50 millimeters in diameter, see for example U.S. Pat. application 
Ser. No. 906,169, filed Sept. 11, 1986, and assigned to the same assignee 
(CHP 6149). 
Inclusions such as cobalt, iron or nickel present in unleached PCD elements 
as residual materials initially used as solvents/catalysts in the 
synthesis of the PCD tend to reduce the temperature stability of the PCD 
to well below 1,200 degrees C., for example, to about 750 degrees C. 
The fabrication of the larger diameter materials requires rather large and 
expensive processing equipment capable of generating high pressures and 
temperatures. The temperatures and pressures are those in the diamond 
forming region of the phase diagram for carbon, see for example U.S. Pat. 
No. 4,108,614 and 4,411,672. The length of the substrate or backing is a 
limitation since the processing equipment must be capable of fabricating a 
diamond facing on a rather long piece which takes up room in the press. 
The result is that in at least one instance, the length of the backing, 
axially to the rear of the PCD face, is rather short and after formation, 
a longer tungsten carbide member or member of other material is attached 
to the formed product by any one of several well known procedures, and as 
described in U.S. Pat. No. 4,200,159, for example. 
In one typical use of these products, for example in oil and gas drilling 
bits and core bits, the usual practice is to form the bit body and 
thereafter to mount the PCD cutting element in the bit body. The bit body 
may be steel and the PCD cutter is a slug type cutter which is press 
fitted into apertures in the bit body. A difficulty with the use of steel 
bodies is that the body may be subject to erosion by the relatively 
abrasive flow of the drilling fluid used to clean and cool the bit. Thus, 
the practice has been to hard face the steel body. 
In the case of matrix body bits which offer erosion resistance, the 
practice has been to mount the slug type PCD cutter by brazing the cutter 
to the matrix body. One of the problems associated with this procedure, in 
addition to the increased cost, is the desire to use a relatively high 
temperature braze material and the need to keep the PCD face cool to 
prevent thermal damage (above about 750 degrees C.) to the cutter face 
during the brazing operation. Even so, a large number of bits have been 
made as described by a variety of bit manufacturers. 
Another commercially available form of PCD, sold under the mark GEOSET, is 
an unbacked leached product, see U.S. Pat. Nos. 4,224,380 and 4,288,248, 
which has a temperature stability of up to 1,200 degrees C., but which may 
have a porosity of up to about 15% and may not be as impact resistant as 
desired in a particular application. The temperature stability of these 
PCD products offers the advantage that they can be exposed to the 
relatively high temperatures used during the infiltration procedure used 
to form the bit body without degradation of the PCD, thus eliminating the 
need for brazing. In general, temperature stability is also an advantage 
in the cutting action of the PCD during use. For the purposes of this 
invention, temperature stability means that the PCD element, regardless of 
type, is stable to about 1,200 degrees C. without significant 
deterioration in its properties and will be referred to herein as TSPCD. 
Temperature stable PCD elements are known which are not porous and are not 
leached. A typical such material, available under the trademark SYNDAX-3 
is a PCD in which silicon is present in the form of silicon carbide. 
Significantly, the TSPCD materials are not commercially available as backed 
products, as contrasted to the previously described low temperature 
products. The TSPCD materials are available as unbacked materials in a 
wide variety of shapes and sizes and they may be cut to form additional 
shapes by using a laser or other means. 
While temperature stability is not required in all uses, there are many 
applications in which it is required. Further, there are processing steps 
such as brazing in which the PCD part may be exposed to temperatures above 
750 degrees C. In these instances it is necessary to cool the PCD part or 
to otherwise prevent it from being exposed to the higher temperature. As a 
result, there are limitations in the processing of such unstable PCD 
products which tend to limit the use thereof. 
TSPCD elements, are available in a limited range of sizes that are 
generally too small for individual use in many applications. To overcome 
this problem, TSPCD elements have been formed into a mosaic type of 
structure in which the individual TSPCD elements are mounted and 
mechanically affixed in a support structure, e.g., a hot-pressed segment 
or the like, see U.S. Pat. applications Ser. No. 797,858; 794,569 and 
797,445, filed respectively on Nov. 14, 1985, Nov. 4, 1985 and Nov. 13, 
1985, and all assigned to the same assignee as this application. 
While these mosaic structures have been operated satisfactorily and provide 
a large PCD cutter having temperature stability, the mosaic elements lack 
the advantages of the large one piece PCD cutters(up to 50 mm diameter or 
more) which are not temperature stable but which have been used in oil and 
gas drill bits and core bits. Even though the bits using the mosaic 
cutters avoid the necessity of having to braze the mosaic into the matrix 
of the bit, the mosaic cutters do not function as a large one piece PCD 
since the individual mechanically mounted TSPCD elements can be broken 
free of the supporting structure. A mechanical type of mounting also 
limits the shape and size and contour of the cutter, even though the 
assembly is temperature stable. 
Another problem with known mosaic cutters is that bending stresses tend to 
cause release of the mechanically mounted TSPCD elements. Moreover, unlike 
a large integral brazed PCD cutter of the same size in which only small 
portions of the PCD are fractured off during use, the tendency in the 
mosaic cutters is to release entire TSPCD elements as the supporting 
structure around the TSPCD is abraded away and support for the TSPCD is 
reduced, i.e., the individual TSPCD element is lost rather than losing 
only a small fragment. 
In general there is a need for a TSPCD containing product in which one or 
more TSPCD elements are firmly anchored or locked into or mounted on a 
suitable support, which optionally may be mounted to another structure. It 
is desirable to mount one or more of such TSPCD elements by more than 
merely a mechanical mounting, and preferably it is desired that the 
mounting be by a firm chemical bond. 
U.S. Pat. No. 3,650,714 of Mar. 21, 1972, issued to Farkas, describes a 
method for coating natural single crystal diamond particles in the range 
of 200 to 250 mesh with either titanium or zirconium. The coating is 
applied from dry powder, the resultant material is then heated in a 
graphite mold, under vacuum conditions for between 10 to 15 minutes at a 
temperature in the range of 850 to 900 degrees C. The relatively low 
temperature of heating to form a carbide at the interface indicates that 
the titanium or zirconium coating is quite thin. The result is said to be 
a coated diamond particle in which the coating is about 5% by weight of 
the resultant product and in which a carbide is formed at the interface, 
with the outer surface of the coating being non-carbided. The calculated 
thickness of the coating is about 0.445 of a micron for 200 mesh material 
and 0.344 of a micron for 250 mesh material. Since subsequent processing 
in an oxidizing atmosphere would result in the formation of an oxide which 
is not easily wetted by other materials, the coated natural diamond 
particles are overcoated with either nickel or copper with a film 
thickness of between 0.002 and 0.005 of an inch (between 50.8 and 127 
microns thick). This outer coating is said to serve as a protective 
coating to prevent oxidation of the titanium or zirconium or their 
carbides during subsequent processing under oxidizing conditions. The 
subsequent processing described is hot or cold pressing and subsequent 
sintering or infiltration with brazing alloys. 
An important difficulty with the above procedure and the resulting product 
is that the carbide containing coating is quite thin, substantially less 
than one micron, with the result that under certain types of subsequent 
processing such as with the use of liquid binders in infiltration, as for 
example in the formation of an infiltrated matrix for earth boring bits, 
the liquid binder penetrates the protective coating and the relatively 
thin carbide containing coating. The problem would be particularly acute 
with PCD elements since their surface is rather "rocky" and irregular and 
includes a certain amount of surface porosity. Thin coatings such as 
described in Farkas would contain substantial imperfections and voids that 
would permit the liquid infiltrating binder to attack the carbide 
interface between the PCD and the coating and to separate the coating from 
the PCD. In addition, the processing of such coated diamonds, whether PCD 
elements or natural, in an oxidizing atmosphere is not practical since any 
imperfection or dissolution of the outer nickel or copper coating, for 
instance by the action of the liquid binder, would result in the oxidation 
and destruction of the underlying titanium and titanium carbide layer. 
Also known in the prior art are products which might be generically 
referred to as diamond impregnated products. Typically these products are 
composed of natural or synthetic diamond particles which may be of a 
variety of mesh sizes. Whereas a large integral PCD element may be between 
70% and 97% by volume of diamond material, depending upon the processing, 
the amount of residual inclusions or porosity, the impregnated products 
generally have a much lower volume percent of diamond, typically less than 
40%. The result is that the impregnated product performs better as an 
abrasive or cutting element than does the same material without the 
diamond grit, but the problem is that the small diamond particles are 
easily lost as the surrounding supporting structure is abraded away. To 
improve the retention of the diamond grit in the supporting structure it 
has been proposed to coat the particles of the grit with various metals 
such as tungsten, tantalum, columbium, niobium or molybdenum, and the like 
by chemical vapor deposition techniques using a fluidized bed procedure, 
see for example U.S. Pat. Nos. 3,871,840 and 3,841,852. The products there 
described are about 25% by volume of diamond grit of particle size from 40 
to 100 mesh and represent an improved impregnated product in contrast to 
an improved large diamond product. The coated diamond grit is formed into 
various shapes by a hot pressing procedure or by infiltration at an 
elevated temperature. 
Coatings have also been used to form diamond products as contrasted to 
impregnated products. For example, U.S. Pat. No. 3,879,901 describes the 
vacuum deposition of a metal such as molybdenum or titanium on diamond 
materials with subsequent processing at 60 Kbar and between 1,200 and 
1,400 degrees C. to form a diamond product. In another instance, see U.S. 
Pat. No. 4,378,975, an abrasive body with diamond is formed by forming a 
green body by cold pressing with a nickel based alloy. The green body is 
then sintered at 950 degrees C. with a diamond volume of between 10% and 
40% by volume. 
It is also known in the sintering of synthetic diamond to use a thin 
coating of between 300 and 6,000 Angstroms of a strong carbide former, 
with a second coating of copper with subsequent processing at 5 Kbar at a 
temperature of 600 to 700 degrees C. in an inert atmosphere, see U.S. Pat. 
No. 3,356,473. In U.S. Pat. No. 3,464,804 it is proposed to form a 
chemically bonded coating of titanium such that a titanium-carbon bond is 
formed followed by processing at 62,000 atmospheres of pressure. 
In general, the coating procedures of the prior art are related to 
pretreatment of diamond forming materials which are thereafter processed 
at relatively high temperatures and pressures to form a diamond element or 
to form a coating on diamond grit used to form an impregnated product in 
which the volume of diamond is well below about 50% by volume. 
The provision of improved methods for the fabrication of large TSPCD 
products, which are temperature stable in the range of about 1,200 degrees 
C. and which may be fabricated at lower pressures and temperatures than 
have been used in the synthesis of diamond products, would have unique 
advantages. For example, the cost for fabrication equipment is vastly 
reduced as well as the cost for each of the products. The ability to 
fabricate various shapes and sizes and thickness, i.e., to be free of the 
shape and size limitations of high-temperature and high pressure 
equipment, would also offer advantages from a processing and application 
point of view. 
One of the significant advantages of the present invention is the ability 
to fabricate a TSPCD product of a particular configuration and in which 
the TSPCD starting element or elements are firmly anchored in place on a 
matrix backing. The term "matrix" is used to describe the powder and 
binder material which is placed around or in contact with the TSPCD 
element and which is processed in accordance with this disclosure. As will 
be described, this matrix may, for instance, be formed either with a 
highly compacted ceramic powder, sometimes referred to as a "matrix 
carrier", such as might be used as a cutter for an earth boring bit, or 
with a non-compacted ceramic powder, such as might form the body of an 
earth boring bit. In either case, the final matrix is formed by 
infiltration with a molten binder alloy or by solid state sintering. 
BRIEF DESCRIPTION OF THE INVENTION 
In accordance with the present invention, a TSPCD product is provided which 
is fabricated from a single or a plurality of TSPCD elements by improved 
low pressure and low temperature procedures. The TSPCD product comprises 
one or more TSPCD elements coated with a carbide forming metal and bonded 
to a matrix. Each TSPCD element is chemically bonded to an inner carbide 
layer of the metal coating, and the metal coating is chemically bonded to 
the matrix. 
The metal coating comprises a carbide forming metal, preferably one which 
is stable against oxidation during processing. The preferred metal 
coatings are the refractory transition metals, especially tungsten, 
tantalum or molybydenum, and most preferably tungsten. Less preferably, a 
double layer coating such as tungsten/titanium or tungsten/chromium or 
nickel/titanium may be used. The metal coating should be at least 1 micron 
in thickness and preferably 3 microns thick. Maximum bond strength is 
obtained with coatings between about 10-30 microns. A carbide layer 
between the TSPCD and the metal coating chemically bonds the coating to 
the TSPCD. The outer portion of the coating remains metal, which is 
chemically bonded to a matrix material. 
A particular advantage of the present invention is the ability to form a 
product made up of a plurality of TSPCD elements that act as a single 
larger TSPCD element bonded to a backing. 
In general, the method of the present invention includes the steps of 
coating one or more TSPCD elements with a carbide forming metal, 
assembling the coated TSPCD element in a mold with a powder of the matrix 
material, such as powdered tungsten carbide, and bonding the TSPCD to the 
matrix material by liquid infiltration with a binder alloy or by solid 
state sintering. 
If the matrix is to be compacted to form a matrix carrier, the assembly of 
the coated TSPCD and the matrix powder can be cold pressed to compact the 
powder to about 50 volume percent. The thus pressed assembly may then 
optionally be cold isostatic pressed to further increase the volume 
percentage of the powder to about 60-65 volume percent. The cold isostatic 
pressed part has sufficient integrity to be handled and machined, if that 
is needed. If the matrix is to form the body of a tool or drill bit the 
compacting steps are generally not necessary. 
Preferably, the carbide layer is formed simultaneously with the liquid 
infiltration or solid state sintering step. However, the coated TSPCD can 
be first heated in a vacuum, inert or reducing atmosphere under carbide 
forming conditions, i.e., at temperatures above about 900 degrees C. to 
form the carbide inner layer before being placed in the mold with the 
matrix powder. 
The term "chemical bond" is used herein to refer to the strong bonds that 
are formed between the diamond and the metal coating through the medium of 
the carbide layer at the interface, and between the exterior surface of 
the metal coating and the matrix carrier. While not fully understood, it 
is believed that the former is an atom to atom level bond between the 
carbon of the diamond and the carbide layer. The latter is believed to be 
a metallurgical bond in which the binder alloy used in the liquid state 
infiltration or with the sintered material of the matrix if solid state 
sintering is used. This contrasts sharply with the mechanical bonds that 
were formed in the prior art systems. 
The term "diamond product" used herein and in the claims includes cubic 
boron nitride. 
The methods described above permit the formation of a wide variety of 
shaped cutting elements for use in various cutting and abrading devices. 
In general, however, the principal advantage of this invention is the 
ability to provide a TSPCD structure in which one or more TSPCD elements 
are firmly anchored in a support structure by a bond which is 
significantly stronger than a mere mechanical mounting. One important 
result is that the assembly of several TSPCD pieces in the form of a 
predetermined pattern results in the part acting as one large TSPCD 
element rather than as a plurality of TSPCD elements held together as an 
aggregrate.

DETAILED DESCRIPTION OF THE INVENTION 
In accordance with this invention, the starting diamond material is 
preferably a TSPCD element composed of aggregate diamond particles having 
a size in the range of submicron to over 100 microns, for example, 
although the particle sizes need not be uniform; i.e., mixtures of 
particles of the sizes indicated may be used as is known in the art. The 
TSPCD should contain at least 60% by volume of diamond aggregates, and the 
product may be leached or unleached with diamond to diamond bonding or 
diamond to metal bonding in the assembly. For products to be used in 
cutting or abrasive operations where the surface finish of the cut or 
abraded part is important, it is preferred that the smaller particles of 
diamond be used, for example, below about 15 microns. By way of example, 
wire drawing dies may require smaller particle sizes in order to provide a 
certain surface finish on the drawn wire product. 
The TSPCD element may be as small as 250 microns, (i.e., 10 mils) on an 
edge and as large as one carat or more. It is preferred that the edge 
length of the starting TSPCD be above 1,000 microns (i.e., one millimeter) 
since pieces of this size are easier to manipulate or handle. Typically, 
TSPCD elements of a size of three pieces per carat (0.165 of an inch per 
side triangles) are easily handled. 
In some instances the smaller particle sizes of TSPCD material below 250 
microns may be used as a grit in the material used to bind the larger 
TSPCD elements described in order to provide an impregnated support or to 
increase the amount of diamond material between adjacent larger TSPCD 
elements. 
It is preferred that the TSPCD starting material be of a regular 
geometrical shape which may be any of the shapes already mentioned. The 
principal reason for a fixed and known geometrical shape is that it 
simplifies the arrangement of the TSPCD elements in the desired 
relationship for processing and thus offers maximum control of placement, 
spacing and overall configuration and content of the final part. Since one 
of the advantages of the present invention is the ability to form large 
TSPCD structures, it is also preferred that the geometrical shape be such 
that the TSPCD starting elements have side surfaces or faces which can be 
positioned in a close and controlled spacing to an adjacent TSPCD element, 
e.g., triangular, square, rectangular and the like, it being understood, 
as will be discussed in detail, that a TSPCD structure may include TSPCD 
elements of different geometrical configurations. 
In the processing in accordance with this invention, as diagrammatically 
illustrated in the flow chart of FIG. 1, the starting TSPCD material 10 is 
preferably cleaned by heating in hydrogen at about 800 to 1,000 degrees C. 
for about 10 to 60 minutes as indicated at 12. Other cleaning procedures 
may be used provided they are effective to remove oxidants and other 
surface contaminants. Thereafter the cleaned TSPCD material is surface 
coated with a metal by any one of several known procedures to form an 
essentially continuous coating which is essentially free of 
discontinuities. For reasons which will become apparent, the presence of 
discontinuities in the coating tends to promote lifting of the carbide 
containing coating off the surface of the TSPCD or provide a defect 
through which other materials may migrate to adversely affect the 
underlying TSPCD. 
One such coating procedure is chemical vapor deposition by which a metal 
compound such as a chloride or a fluoride is heated to decompose the 
compound to form a mist of the metal which then deposits on the TSPCD 
material. Another procedure is fused salt bath coating methods. 
The preferred carbide forming metals for the coating are the refractory 
transition metals, particularly tungsten, tantalum and molybdenum. Less 
preferably, the TSPCD element may also be double coated such as with 
tungsten/titanium, tungsten/chromium or nickel titanium. The use of a two 
layer coating increases expense and the use of oxidation sensitive metals, 
such as titanium, requires special process conditions. Tungsten is most 
preferred as the coating metal because it is a strong carbide former, not 
subject to excessive oxidation damage, has similar thermal expansion 
characteristics as the TSPCD elements, and is not easily dissolved by the 
liquid binder metals during later processing. Other less preferred metals 
that may be used in a given application are the other ones of the Group 
IVA, VA, VIA, VIIA metals and alloys and mixtures thereof and silicon, 
such as titanium, niobium, vanadium, zirconium, manganese, 
molybdenum/manganese, or tungsten/manganese. These materials have a 
melting point higher than the temperatures used in subsequent processing 
and are strong carbide formers and form a strong bond to the diamond. 
Metals of Group VIIIA, such as cobalt, iron and nickel are less preferable 
because of the tendency to weaken the TSPCD by back conversion of the 
diamond or possibly by other means. Zirconium and titanium have been 
observed to have a volume expansion in response to elevated temperatures 
which is more than that of diamond but less than that of cobalt and iron, 
but these materials are subject to oxidation damage in subsequent 
processing in normal atmospheres unless protected by an overcoating of 
nickel or copper or some other material. Even so, care must be taken to 
assure that the carbide containing coating is sufficiently thick to 
prevent penetration by the surrounding metal should the copper or nickel 
or other coating dissolve into the matrix carrier. 
For chemical vapor deposition, one may use the hexahalides, tetrahalides, 
pentahalides, e.g., the hexa-, tetra- and pentaforms of the bromides, 
chlorides fluorides of the metals mentioned. The thickness of the coating 
on the TSPCD element should be at least 3 microns and preferably in the 
range of about 10 to 30 microns. Thicker coatings may be used but do not 
seem to increase the bond strength over that achieved in the range of 
about 10 to 30 microns. In the case of tungsten, a thinner coating, at 
least 1 micron in thickness may be used in certain less demanding 
applications because of its stability and wetting character. 
The application of the coating does not necessarily result in a chemical 
bond to the TSPCD at this point in the processing. As near as has been 
determined, the processing temperature used in chemical vapor deposition 
is not sufficiently high to form a chemical bond as indicated by the 
essential absence of any diffused carbon into the metal of the coating and 
the absence of any metal of the coating being diffused into the TSPCD. 
While it is believed that the coating is essentially uniform in dimension 
and essentially covers the entire outer exposed surface of the TSPCD, it 
is not essential to form an absolutely continuous coating. In the case of 
porous leached TSPCD elements, the coating should be thick enough to 
bridge over the pores in the TSPCD surface so that it is effectively 
coated with the metal. 
The carbide layer may be formed either by heating the coated TSPCD elements 
under carbide forming conditions either before being assembled with the 
matrix forming materials or simultaneously with the formation of the 
matrix by infiltration or sintering. In either case the heating is 
controlled to promote formation of a relatively thin carbide layer on that 
portion of the surface of the TSPCD which has been coated by the carbide 
former. During the controlled heating, under carbide forming conditions, 
carbon diffuses from the PCD into the coating to form a carbide. The 
thickness of the carbide layer is thinner than that of the coating and 
less than 10 microns and preferably less than 5 microns. 
During the heating, it is believed that the temperature used to form the 
carbide is more important than the rate of heating. The evidence suggests, 
in the case of a tungsten coating for example, that the coating on the 
diamond can form a carbide above about 950 degrees C. and preferably at 
about 1,100 degrees C. no matter how fast the heating is conducted. Thus, 
heating at 1,100 degrees C. for about 15 minutes is normally sufficient. A 
longer time of heating at 1,100 degrees C. can increase the thickness of 
the carbide, but in general longer heating periods at high temperatures 
may damage the diamond because of too much carbide formation and results 
in an ineffective chemical bond being formed. Heating at 1,200 degrees C. 
for one hour has been used effectively where the carbide layer is formed 
simultaneously with the bonding of the coated TSPCD element to the matrix 
of a drill bit during the infiltration of the matrix. A vacuum of 10 to 
the minus 6 torr. or a protective atmosphere may be used during heating 
but is not required in all cases. Coatings of less than 1 micron result in 
unacceptable separating of the coating from the TSPCD element during 
infiltration or sintering. The resulting TSPCD element has an outer 
surface coating of the metal chemically bonded to an intermediate carbide 
layer, which in turn, is chemically bonded to the base TSPCD. 
When a tungsten coated TSPCD element is furnaced in a graphite mold or 
oxidative environment, the tungsten is relatively stable against oxidation 
as compared to titanium, for example, unless the titanium is protected by 
an overcoating. In addition to the above noted problems with titanium and 
double coatings, if the overcoating is not continuous, for example if 
there are defects which expose portions of the underlying oxidation 
sensitive coating, subsequent processing in an oxidizing environment may 
destroy the metal and the carbide interface or a local portion of the 
underlying diamond material or both. There are some types of matricies 
which tend to dissolve the oxidation protective layer with the result that 
a gap tends to form between the partially oxidized carbide former coating 
and the surrounding structure, resulting in a marked reduction in the 
strength of the bond between the coating and the surrounding structure. 
Ideally, the bond between the outer surface of the coating and the matrix 
carrier is a metallurgical bond which is not easily formed if the coating 
is not of compatible material or if it is oxidized. 
An important advantage of this invention is the ability to form a backing 
or supporting structure for the TSPCD elements of widely varying 
configuration and composition. The backing is formed in situ as the TSPCD 
elements are bonded chemically together and to the matrix support 
structure. 
In the case where the TSPCD element or elements are to be bonded to a 
matrix carrier, it is preferred to compress the powder and the TSPCD 
elements in an axial compression operation. Ultimately the backing or 
support structure will achieve a volume percentage of metal and/or metal 
carbide and/or abrasive particle (e.g., oxides or non-metal carbides) 
which is in the range of 40% to 80%. Optionally, the compacted structure 
may be further compressed by isostatic pressing in which the volume 
percentage is increased to about 60% to 90%. If the structure is to be 
sintered, isostatic pressing is preferred. 
The hard ceramic powders used to form the matrix carrier may be a metal 
carbide such as tungsten carbide, titanium carbide, tantalum carbide, 
molybdenum carbide, and cemented tungsten carbide (tungsten carbide 
cemented with cobalt). Alternatively, it could be made of other hard 
ceramic powders such as alumina or titanium or silicon nitride. The 
abrasive particles may be alumina, silicon carbide or silicon nitride. For 
applications such as earth boring bits, where strength and toughness are 
important, tungsten carbide is the preferred hard ceramic powder. 
The particular powder used and the particle size or sizes is related to the 
desired volume percent of the matrix powder, the final product which in 
turn is related to the hardness (rigidity) and impact resistance 
(toughness) of the backing or support structure. Also a consideration is 
the type of processing, e.g., liquid state infiltration or solid state 
sintering. 
In the case of liquid state infiltration, the hard ceramic powder, for 
example tungsten carbide, has a particle size which is typically below 325 
mesh (Tyler), i.e., below 44 microns (Standard), for example 30 microns. 
The size distribution and the percentage distribution may vary depending 
upon the supplier. However, the size may also be varied. For example the 
same packing efficiency may be obtained by appropriate selection of 
particle sizes, e.g., 30 microns and 6 microns in a ratio of 70% to 30%. 
A preferred infiltrating material is a copper-tin-nickel-manganese alloy. 
If the alloy does not include manganese or nickel, thinner coatings of 
about 1 micron may be used, as will be discussed. 
In the case of solid state sintering, for example, using a tungsten powder, 
the powder particles are preferably coated with a metal such as nickel, 
for example 0.35 weight percent. This may be done, for instance, by mixing 
tungsten powder of a particle size of 0.5 microns with a solution of 
nickel nitrate in alcohol, followed by heating at about 90 degrees C. to 
evaporate the alcohol with the result that the nickel nitrate is deposited 
on the tungsten powder. The nickel nitrate coated tungsten powder is then 
heated at about 800 degrees C. for about 3 hours in a reducing atmosphere 
(hydrogen) to eliminate the nitrate. The processed tungsten powder is then 
ball milled for about 24 hours using tungsten rods as the milling media 
and then sieved and screened to 200 mesh (74 microns). The purpose of the 
nickel is to act as a diffusion activator for the tungsten. Other binder 
materials which may be used are tantalum, molybdenum, and nickel based 
alloys, copper-nickel alloys and cobalt based alloys. In either liquid 
state infiltration or solid state sintering, the appropriate powder of the 
appropriate particle size or sizes is mixed with a temporary binder 
material which is preferably an organic material as indicated at 15. The 
temporary binder is used to coat the powder material to form a temporary 
adhesive bond between the powder particles during the initial compression 
step. Since this temporary binder remains in the processed product through 
the cold isostatic pressing operation, it should preferably be a material 
which is present in a relatively low volume percentage. If the volume 
percentage of the temporary binder needed to achieve a temporary bond is 
too high, this may affect the volume percentage of the powder in the final 
product, i.e, too great an amount of the temporary binder may prevent the 
achievement of higher powder volume percentages. Various organic polymeric 
or resinous binders which are easily volatilized at elevated temperature 
may be used. A preferred material is paraffin which is easily dissolved in 
an organic solvent. The amount of paraffin relative to the tungsten 
carbide is about 2 weight percent. The paraffin is easily and completly 
removed in the processing. It is also desirable to use a lubricant which 
may be volatilized completely at elevated temperatures in order to 
facilitate powder movement during the various pressing operations, 
especially the optional cold isostatic pressing operation. One such 
material is mineral oil which may also be dissolved with the temporary 
binder to coat the powder. A typical useable amount is 20 grams of 
paraffin per 1,000 grams of cast carbide in 0.2 grams of glycerine per 
1,000 grams of cast carbide, by way of example. 
The powder is dispersed into the solution of the temporary binder and 
lubricant in hexane (for the paraffin) and the binder and lubricant coat 
the powder which is then dried and reground into a powder. Other coating 
procedures may be used as is known in the art. 
The next step in the sequence, as indicated at 20, is to arrange the coated 
TSPCD elements in the desired relationship as needed to form a product. If 
the product is to contain multiple TSPCD elements it is preferred to use a 
template or die configured to position the TSPCD elements with respect to 
each other. The spacing between adjacent TSPCD elements may vary widely, 
depending upon the configuration and nature of the final product. Where 
the part includes multiple TSPCD pieces, the side faces of the TSPCD 
elements may be spaced from each other to provide a gap of from about less 
than 1 mil to 500 mils and preferably in the range of 6 to about 30 mils 
(150 to 750 microns), by way of example. Thereafter, the processed powder 
is placed in the gaps between the adjacent TSPCD pieces and filled in in 
contact with the surfaces of the TSPCD elements to be bonded to the matrix 
carrier. 
In some instances it is not necessary to form a gap as described since the 
TSPCD may be assembled with adjacent surface portions in contact with each 
other. In this instance, where liquid state infiltration is used, the 
binder penetrates between the TSPCD elements and chemically bonds the 
adjacent coated TSPCD elements together. Such a butting arrangement the 
TSPCD's may be used where erosion is not a potential problem, e.g., in 
bearings, saw blades and wire dies and the like, for example. Where 
erosion is likely to be a problem, such as exposure to relatively high 
velocity flow or the use of abrasive materials, the use of a gap in which 
powder is present is preferred for erosion resistance. 
The thus assembled TSPCD-powder temporary assembly is then assembled into a 
pressure die of suitable configuration which preferably defines the 
outside contour of the finished part. One manner of carrying this out is 
to use an open ended die, invert the die and move the temporary assembly 
of TSPCD elements up into the bottom of the die, re-invert the die right 
side up so that the assembly is in the bottom of the die and then add the 
processed powder material to the required volume. The amount of powder 
added is related to the thickness of the support or backing and the volume 
percentage of the metal in the final product. 
The assembled material is then axially cold compressed in the die, as 
indicated at 22, at a pressure of between 10,000 psi and 30,000 psi to 
increase the tungsten carbide packing density to about 50 to 65 volume 
percent. As a result of this processing, a compacted intermediate is 
formed which is fragile but still capable of being handled with care. As 
another example, if the subsequent processing is solid state sintering, 
pressures around 10,000 psi may be used and the resultant product has a 
packing density of about 50 volume percent. 
An additional step in the processing is the cold isostatic pressing 
operation, as shown at 24, in which the compacted intermediate is 
isostatically cold pressed at a pressure of up to about 30,000 psi for 
five minutes or longer, for example. The isostatic pressing typically 
achieves a tungsten carbide packing density of about 62 volume percent. In 
the case of tungsten powder in solid state sintering, the density is about 
65 volume percent. During this operation, the tungsten or the carbide 
powders are moved and compacted uniformly to a more dense product. The 
step of cold isostatic pressing is optional although in many cases it is 
preferred particularly for sintered products. 
At this point in the processing, two alternate processing routes are 
available, as indicated in the dotted lines of FIG. 1, liquid state 
infiltration, as seen at 26 or solid state sintering as seen at 28. 
In the case of solid state sintering, the product of the isostatic pressing 
is sintered in a vacuum furnace at 10 to the minus 5 torr. at 1,200 
degrees C. for about 1 hour. The result is a sintered product having a 
density of about 90 volume percent. The finished product indicates a bond 
between the tungsten material with the tungsten coating on the TSPCD, 
i.e., a tungsten-tungsten metal bond. The nickel or other activator is 
used to promote diffusion and metallurgical bonding. The mechanical 
properties of this bond are quite strong, and the finished product, 
although somewhat brittle is quite useable. 
There are, however, some limitations of solid state sintering. For example, 
the limitation of sintering at a temperature below 1,200 degrees C. 
renders it difficult to find a material with high strength and high 
modulus. Even if the high modulus materials can be sintered below about 
1,200 degrees C., as by activation sintering, the sintered product may 
contain 5% or more porosity which may act as pre-existing cracks. While 
this may not be a problem in some cases, it is a consideration where the 
finished part is in a part which is subject to relatively high impact 
loads, e.g. a drill bit for example. 
In those instances in which the bonded TSPCD product is to be mounted to a 
high modulus backing, the processing may involve two thermal cycles to 
bond the TSPCD product to a tungsten carbide back-up element. While 
effective, the processing steps increase the costs. 
Even though these problems exist, the advantage of this form of processing 
is the ability to provide a high strength, low thermal expansion material 
to bond the TSPCD together. There are known ductile materials which may be 
added to the powder or the binder in accordance with this invention to 
decrease the brittleness of the sintered matrix carrier. 
It is preferred to use liquid phase infiltration as the last process step. 
In this processing, the product from the isostatic pressing operation is 
heated to cause a metal binder to flow through the compacted powder and 
bind it together and to the TSPCD elements. 
Regardless of the type of processing as herein described, the hard ceramic 
powder in the matrix carrier can be of relatively high volume percentage, 
e.g., above 50% and up to 90% by volume. The provision of a relatively 
high density final product, which is formed in situ at relatively low 
pressures and temperatures and which is temperature stable to about 1,200 
degrees C. offers advantages not heretofore obtained. 
The metal binder material should be one which in a liquid state can wet the 
coating on the TSPCD and the hard ceramic powder particles. It is also 
preferred that the binder metal have good mechanical properties such as 
ductility and strength. Typical such binders are copper or nickel based 
brazing alloys, copper-tin-manganese-nickel alloys, the latter being the 
preferred binder material. 
The processing above described, as already noted may be used to form a wide 
variety of products which are characterized as having a strong chemical 
bond between the coating and the TSPCD and between the coating and the 
supporting structure. It is this chemical bonding which provides the 
significant strength over that which can be achieved by merely a 
mechanical gripping of the TSPCD. The advantage of this invention is that 
the TSPCD elements or element are effectively locked in or on a support 
structure to provide a TSPCD cutting element as contrasted to the prior 
temperature sensitive supported TSPCD elements commercially available. 
Referring to the drawings which illustrate preferred forms of the present 
invention, FIG. 2 illustrates a TSPCD product 30 which includes six (6) of 
initially separate TSPCD elements 31a to 31f of generally triangular 
shape. The TSPCD elements may be bonded together in or on a support 
structure 32, see also FIG. 3, which may be an infiltrated or sintered 
powdered material. The support structure may be of various dimensions and 
of various axial lengths, as indicated by the break line 33. 
As seen in FIGS. 2 and 3, the TSPCD elements include at least one side face 
34a which may be positioned adjacent to but spaced a small distance from 
the side face 34b of the adjacent TSPCD element. The distance between 
adjacent TSPCD elements, referred to as the gap and illustrated as 35 in 
FIG. 3, may be of the dimensions previously indicated. 
Referring to FIG. 4, for example, the gap 35 is illustrated with reference 
to its condition after cold isostatic pressing and before further 
processing. Each of the TSPCD elements 37 and 38 includes the coating 37a 
and 38a, respectively, the TSPCD elements being spaced from each other by 
the gap width. Between the coated surfaces is the powder material (not 
shown) such that the gap is TSPCD face-coating-powder-coating-TSPCD face. 
In subsequent processing, a strong chemical bond is formed from the TSPCD 
face through the coating, through the powder, through the coating of the 
adjacent TSPC face and to the adjacent TSPCD. 
Again referring to FIGS. 2 and 3, in the resulting TSPCD product 30, 
essentially all surfaces of the TSPCD elements, save one, are in contact 
with bonded support material, i.e., there is material on the bottom face 
41 and peripherally around the outer faces, as indicated at 42 and in the 
gap 35, while one face 44 is exposed. This form provides the optimum 
bonding of the TSPCD elements together. This product may be assembled to a 
bit body during infiltration of the bit to form the matrix bit body. It is 
also possible to braze the product into the bit body, in which event, 
higher temperature braze alloys may be used than have heretofor been used. 
The form of TSPCD product in accordance with this invention shown 
diagrammatically in FIG. 5 illustrates that not all of the faces need be 
fully in contact and bonded to the support element. Here a triangular 
TSPCD element 50 includes side faces 50a, 50b and 50c which are only 
partially beneath the top surface 52 of the support structure 53 shown as 
triangular for purposes of illustration. Due to the strong chemical 
bonding between the TSPCD element and the support structure, it is 
possible to expose a substantial portion of the large flat face 50d of the 
TSPCD element while the body of the TSPCD element is substantially above 
the support body. Thus, for example it is possible in accordance with this 
invention to form large bearings from smaller TSPCD elements. 
Referring to FIGS. 6 and 6a, for example, a TSPCD product 60 is illustrated 
which may be used as a bearing or the like. This form of product also 
illustrates that TSPCD elements of different geometrical shapes may be 
used to form useful TSPCD products. In this form, TSPCD elements 61 and 63 
are half circular disks while TSPCD element 64 is square, although it may 
also be rectangular. The TSPCD elements are bonded to a support 65 of 
metal powder processed as already described with gaps 66a and 66b between 
adjacent elements. As illustrated the gaps, however, are not filled with 
matrix carrier material thus effectively providing channels between the 
spaced and facing exposed side faces 61f-64f and 64g-63f, the elements 61, 
63 and 64 being positioned such that a substantial portion is exposed as 
noted with reference to FIG. 5. When used as a bearing, the channels may 
provide for flow of cooling or lubricating fluid, if desired. If channels 
are not needed, the gaps may be substantially filled as illustrated in 
FIG. 3, i.e., the surface of the support is even with the top surface of 
the TSPCD elements. 
Not all of the side faces need be in contact with and bonded to the support 
material. Thus, for example as illustrated in FIG. 7, a single point 
dressing tool 70 is shown which includes a TSPCD element 72 mounted on and 
bonded to a support 74 such that one face 72a is fully contacted by the 
support material which effectively forms a shoulder 76 to the rear of the 
element 72. Faces 72b and 72c are fully exposed while the bottom surface 
is bonded to the support. While element 72 is indicated as triangular, it 
may be other shapes such as square, rectangular, semi-circular or 
circular, for example. 
The ability to bond a TSPCD element firmly in a support structure permits 
the fabrication of unique cutting and abrading products. For example, 
FIGS. 8 and 8a illustrate an improved saw blade segment 80 composed of a 
plurality of TSPCD elements 81a through 81k, bonded to a support structure 
83. In the form illustrated, the TSPCD elements are circular in shape 
although other geometrical shapes may be used. Circular shapes, however, 
have the advantage of providing a relatively large surface area for firmly 
bonding the elements to the support structure. The diameter of the 
elements may be in the range of one millimeter or larger depending upon 
the use of the segment. Prior art saw blade segments were either 
impregnated with diamond dust or used spherical natural diamonds. In the 
either case as the supporting matrix carrier was worn due to use, the 
diamond material was lost due to loss of supporting structure. This 
problem is largely overcome by the present invention since the TSPCD 
elements are firmly chemically bonded over a comparatively large surface 
area. 
The TSPCD elements are preferably arranged in a redundant pattern such that 
elements 81e through 81g are to the rear and in the space between the 
adjacent lead elements 81a-81d, with elements 81h-81k oriented in the 
spaces between 81e-81g. Thus, for example if the thickness of the elements 
is equal to or greater than the gap dimension between adjacent 
side-by-side elements 81a-81d, the entire face of the cut in the workpiece 
is traversed by at least one cutter. The redundancy may be two or more, 
that is, additional elements may be arranged to provide added redundancy 
as may be needed. 
As illustrated in FIG. 8a, each element 81a-81k includes an exposed arcuate 
cutting face, for example 81aa, 81ee and 81hh extending above the surface 
84 of the support 83, with a substantial portion of each element firmly 
and chemically bonded to the support. As the segment wears in use, the 
elements are retained to a much greater degree than the prior diamond 
cutting segments. While circular elements have been described, one may use 
a half-circle or quarter-round TSPCD elements, preferably mounted such 
that the curved peripheral surface is exposed to form the leading cutting 
edge. Such materials are commercially available or may be cut off a 
cylindrical TSPCD part to the desired thickness. 
The ability to anchor and firmly bond a TSPCD element to a support 
structure permits the fabrication of a wide variety of cutting and 
abrading tools. It also permits the fabrication of products that are other 
than abrading or cutting tools, such as bearings, as described and, for 
example, a lead bonding tool. Heretofore, lead bonding tools have been 
made of a single crystal diamond cut to a precise shape and dimension with 
a flat working face. Typically these tools are used to bond lead elements 
to solid state chips and the like by being brought into contact with the 
chip and bonding the leads in a precise and exact location to the chip 
through heat and pressure. Normally the temperature is about 500 degrees 
C. and natural diamonds are able to withstand this temperature. However, 
it is difficult to support these natural diamonds in a support structure 
and if they move even slightly, problems may be encountered in their use 
since the bonding operation requires precision. In accordance with this 
invention, an improved lead bonding tool is provided which is firmly 
anchored in a support structure and which is temperature stable. 
Referring to FIG. 9, an improved lead bonding tool 90 is illustrated and 
includes a TSPCD element 92 bonded to a support structure 94, the latter 
being metallic and including an aperture 95 therein for a heater and 
including a shank 96 for mounting in the lead bonding machine. The support 
usually includes a cylindrical section 97 having a frusto-conical end 98 
with the element 92 mounted at the tip of the end 98. The element 92 
includes a working face 99 which projects beyond the end 98 and which is 
of a precise flatness and face dimension, i.e., length and width. The face 
contour may be square or rectangular, or any other shape, as may be 
desired. Heat may be applied to heat the element in a conventional manner 
normally used to heat the lead bonding tool. In use the tool is subject to 
vibration and heat which requires that the element be firmly and 
accurately mounted and maintained in that accurate mounting during use. By 
the present invention, the TSPCD element 92 may be chemically bonded to 
the support structure which may be the support 94 or a separate insert to 
be received in the support. The advantage of this invention is that a 
TSPCD element may be used which may be relatively easily affixed to a 
support structure. 
Thus, for example, the element 92 may be shaped to the precise required 
length and width dimensions and in situ bonded to a support structure. If 
the support structure is the support 94, the face of the TSPCD may be 
precision ground to the desired flatness such that the plane of the face 
99 is referenced to the support structure, an operation which is difficult 
to achieve with single crystal diamonds. It is also possible to form a 
lead bonding tool by formation of a TSPCD support structure which is then 
assembled to the body 94, rather than forming the entire assembly in one 
step. 
One aspect of this invention is the ability to form a TSPCD product of 
virtually any shape or size from smaller TSPCD elements. The TSPCD product 
illustrated in FIG. 10 is an example. There a large TSPCD product 100 is 
composed of a multiplicity of triangular TSPCD elements 101 in a TSPCD 
part which is essentially circular in overall shape, although it may be of 
any shape. In the form illustrated, there is a surrounding portion 105 of 
tungsten carbide, for example. The tungsten carbide may be of 70 volume 
percent tungsten carbide. By way of example, the part may be 50 mm in 
diameter and is useful as a cutter for oil and gas drill and core bits. 
FIG. 11 illustrates another TSPCD product 110 in accordance with this 
invention composed of a plurality of TSPCD elements 112 illustrated as 
being triangular pieces which may be for instance 3 per carat or 1 per 
carat. The elements 112 are bonded together and to a support 115 such as 
tungsten carbide by any of the methods already described, so as to form a 
unitary structure in which the previously separate elements are chemically 
bonded together and to the tungsten carbide and to the tungsten carbide 
backing 115. It is understood that the backing may be any of the carbide 
materials already described. 
The form of the invention illustrated in FIG. 11 illustrates the variety of 
TSPCD products that may be fabricated in accordance with this invention. 
This particular structure provides for a plurality of cutting elements 
112a and b, 112c and d, and 112e and f, which form pairs which together 
provide a series of cutting points 116, 117 and 118. In use in a bit, as 
shown in FIG. 11a, the cutting product 110 may be mounted directly into 
the body matrix during body matrix infiltration or formation. In this 
form, there is a back support 121 provided which contacts the backing 115, 
the cutting direction being indicated by the arrow 123. The tungsten 
carbide backing 115 provides for increased impact strength. 
The cutting product 110 is exposed such that at least one top row of 
elements 112a-112f are essentially fully exposed. In use as the top row of 
cutters wear, new cutting surfaces are regenerated from the cutter 
elements below the top row. This product also illustrates the fact that 
adjacent elements include at least one side surface which is located 
adjacent to the adjoining piece, the spacing being as already described. 
To improve the cutter performance in terms of regenerating cutter edges and 
points, the amount of matrix carrier between adjacent TSPCD elements may 
be reduced in cross-sectional thickness in order to provide controlled 
weakness planes in the cutter structure thereby providing for fracture of 
the cutter along predetermined planes of fracture. In this way as the 
loading on a cutter region increases, the cutter is broken out of the 
support to provide a new cutter element. Since earth boring, in part, 
relies upon a kerfing type of cutting, the formation of an uneven overall 
cutting surface generally tends to improve the cutting action in certain 
types of formations. 
As already noted, the products of the present invention are much stronger 
than products previously described as mechanical mosaic structures. 
Referring to FIGS. 12a to 12d, FIG. 12a illustrates diagrammatically a 
three point bending test in which loads are applied to a part 130 in one 
direction as indicated by the arrows 131 and 132 and a load is applied in 
another direction as indicated by the arrow 133. The force necessary to 
bring about fracture through the joint 135 or through the joined parts 136 
is measured and expressed in terms of pounds per square inch to failure. 
FIG. 12b illustrates a TSPCD part 140 in accordance with this invention 
made up of triangular TSPCD elements 141 joined together as indicated at 
the joints 142 by the methods already described. The part 140 was 
processed by sintering tungsten coated 3 per carat TSPCD elements with 
tungsten powder which had been compressed to a volume percentage of 90%. 
In the three point test, the failure mode was in the joint between 
adjacent elements, as indicated at 145. The load to failure was 21,000 
psi. 
FIG. 12c is similar in structure to that of FIG. 12b, but the part 150 was 
formed from tungsten coated 3 per carat TSPCD elements which were liquid 
state infiltrated with tungsten carbide using a copper binder, as 
described, and processed as described. In the three point test, the 
failure mode was through the TSPCD as indicated at 155 and the load to 
failure was 26,000 psi. 
FIG. 12d illustrates a mechanical mosaic structure 160 which is essentially 
the same as 150, but in which the TSPCD elements were not coated and in 
which the part was processed using conventional infiltration techniques 
with the same tungsten carbide and binder used to form the part 150. In 
the three point test, the failure was through the joint, as indicated at 
165, and the load to failure was zero psi. 
Other test data indicates that the thickness of the carbide forming coating 
is significant. These data were derived from the use of a matrix material 
in which the binder included nickel and manganese. In the case of tungsten 
coated material, it has been observed that nickel and/or manganese tend to 
adversely affect the coating if the coating is too thin, for example below 
about 3 microns. However, if the binder for the matrix is copper or tin or 
combinations thereof, thinner coatings of one micron may be used for less 
demanding applications. If the binder for the matrix is from the iron 
group, e.g., nickel or manganese, somewhat thicker coatings are needed to 
prevent the binder from penetrating the coating on the diamonds. 
For example, in a shear test where coated TSPCD is bonded to a matrix 
carrier, as described, and subject to a lateral pushing force, the results 
indicate that in the range of 1 to 5 microns, there is improvement in the 
bond strength to about 5,000 psi. The failure mode at this range of 
coating thickness is by failure at the interface of the coating and the 
matrix carrier. In the range of about 5 to 7 to about 8 to 10 microns 
thickness, the fracture is mixed in nature, in that the fracture sometimes 
is at the stated interface and sometimes through the TSPCD. The stated 
fractures occur at bond strengths in the range of about 5,000 psi and up 
to about 23,000 psi. In one example with a 9 micron tungsten coating a 
bond strength of about 23,000 psi was measured. In this range of bond 
strengths, the TSPCD product in accordance with this invention has a wide 
variety of uses. Above about 10 microns, the fracture mode is through the 
TSPCD element and not through the bond, i.e., this means that the 
interfaces between the PCD and the coating, the coating and the bond, the 
coating itself and the bond itself are all stronger than the PCD. These 
fractures of the TSPCD element, rather than at the interface between the 
support structure and the TSPCD element occur typically at strengths in 
the range of above about 22,000 to 23,000 psi, Above about 15 microns of 
coating thickness, the bond strengths seem to level off at about 27,000 to 
29,000 psi, with fracture through the TSPCD element rather than the bond 
interfaces, even though the coating thickness increases to 20 microns or 
more. For coating thicknesses above about 30 microns, there does not 
appear to be any increase in bond strength over that achieved in the range 
of 15 to 30 microns. 
By way of further comparison, a titanium carbide coated TSPCD element 
having a thickness of about 5 to 10 microns, typically at 7 microns, and a 
total coating thickness (including a nickel oxidation protective coating) 
of about 30 to 50 microns exhibited mixed failures through the bond and 
through the TSPCD element at about 15,000 psi. These data also tend to 
establish that a tungsten coating, absent any oxidation protective 
coating, having the thickness dimensions described, is superior to 
products with a titanium carbide coating and a nickel protective coating. 
The achievement o sufficiently high bond strengths to result in the 
failure of the TSPCD rather than the bond of the latter to the supporting 
structure offers considerable advantages, especially in the cases of those 
products which require a strong bond of a cutter-type product in some form 
of support structure. 
Referring to FIG. 13, there is illustrated a product 170 which includes a 
TSPCD element 172 firmly secured to a tungsten carbide support element 
174. While the product 170 superficially resembles the appearance of a 
prior art non temperature stable PCD cutter, it is quite different. 
More specifically, the TSPCD element may be a product available 
commercially as SYNDAX, a TSPCD material in the form of a thin one-piece 
disc. The dimensions of the disc 172 may vary widely from a diameter of 2 
to 3 mm to as much as 50 mm or more. The disc 172 is firmly chemically 
bonded to the support element 174 through the chemical bond formed through 
the coating applied to the disc 172 which in turn is bonded to the 
infiltrated or sintered material 175. 
The support 174 may be separately formed and the disc 172 and the material 
175 may be assembled and processed as described. The result is the 
chemical bonding of a TSPCD to a preformed support. The advantage is that 
the length, diameter and shape of the support is not limited by the size 
of the high pressure high temperature presses normally used to form prior 
art products. The cost for making such a product is less than that for the 
non temperature stable product, but a more important advantage is the 
ability to form the support of essentially any length, as indicated by the 
break line 176, without requiring larger presses. This form of product 
also has the advantage of being temperature stable up to about 1,200 
degrees C. and may thus be infiltrated simultaneously with the formation 
of a supporting matrix, for example a matrix body for a drill bit. 
Alternatively, the product may be brazed into the bit body by the use of 
higher temperature brazing materials than have been heretofore used. It is 
also understood that the coated diamond may be brazed to a suitable 
support such as cemented tungsten carbide, and the like, since the braze 
joint is between the coating on the diamond and the support element. Since 
the diamond is temperature stable higher melting point brazing alloys may 
be used as compared to those alloys which are used with diamond product 
which are not temperature stable, as herein defined. 
As illustrated in FIG. 13, the side surface 178 of the disc is free of 
sintered or infiltrated material. In the form illustrated in FIG. 13a, the 
sintered or infiltrated material may cover the sides of the disc 172a, as 
indicated at 179 for added strength. 
FIG. 14 illustrates a structure in which one or more TSPCD elements 180 are 
affixed to a supporting body such that the back side 183 of the elements 
are in contact with the support body while the side faces are adjacent to 
each other or include a fully exposed side face, as indicated at 187. In 
this particular case, the support body may be a saw blade segment or a 
preformed and preshaped cutter for an earth boring bit. While the 
configuration of the product illustrated in this figure may appear similar 
to some of the illustrations of U.S. Pat. No. 3,938,599 issued to Horn, 
there are significant differences. Unlike the Horn structure, that of the 
present invention is chemically bonded to the supporting matrix carrier 
and is far stronger than a mere mechanical bond as described in the 
referenced patent, see also the data previously described. This strong 
bonding allows for the provision of a variety of products. 
Thus, for example, FIG. 15 illustrates a twist drill 190 having segments 
192 and 194 mounted thereon. Segments 192 and 194 may be a TSPCD product 
in accordance with this invention containing one or more TSPCD elements in 
a support structure. The drill bit may be of a 1/4 inch or larger size. 
FIG. 16 illustrates a form of the invention similar to that of FIG. 13 
wherein the TSPCD elements 200 are square in shape. The TSPCD elements are 
bonded to each other through the material 201 and to the base 202, as 
described. The base may be of a shape other than square and may be of any 
length as indicated by the break line 205. 
FIGS. 17 and 18 illustrate a drill bit 220 in accordance with the present 
invention. The bit includes a body 222, preferably of matrix material such 
as carbide, having a plurality of waterways 225 associated with a 
plurality of blades 230. It is to be understood that in referring to the 
bit body as a matrix body, the matrix material of the bit body may be a 
relatively thin coating on a suitable support structure. The bit also 
includes nozzles 235 for flow of fluid form the interior of the body to 
the waterways to cool and clean the bit. 
As shown in FIG. 18, each blade includes a plurality of cutters 240 having 
a configuration as illustrated in FIG. 2, for example. The cutters 240 are 
mounted in the matrix body during infiltration of the body thus 
eliminating the need to braze the individual cutters into the bit body. As 
mentioned, each of the cutters, by virtue of the production thereof is 
temperature stable to 1,200 degrees C. It is understood that other cutter 
configurations in accordance with this invention may be used, for example 
that illustrated in FIG. 10 or in FIG. 13, for example. It is also 
possible to provide cutters of selected geometry, e.g., quarter circles, 
half circles and the like. 
In FIG. 19, the coated TSPCD 250 is assembled to a matrix support, as for 
example a matrix body drill bit 252. It is to be noted that essentially 
the entire face 253 of the triangular element is above the matrix as 
compared to the prior designs. This arrangement is possible because in 
accordance with this invention, there is a bond between the surfaces of 
the TSPCD in contact with the matrix and the opposed surfaces of the 
matrix. While a backing structure 255 is illustrated, both the side faces 
256 and the front face 253 are fully exposed. In this way, the cutter may 
be mounted such that there is total full face exposure. 
Drill bit or core bit bodies may be of any of a number of types, as is 
known in the art. Thus, for example, stepped bit designs may be used with 
a significant cutter exposure. The ability to fabricate cutters to 
different desired geometries as may be needed for effective cutting action 
in various formations is now possible in accordance with this invention. 
Typical processing of TSPCD elements in accordance with this invention is 
set forth in the following specific example, by way of illustration. 
Triangular temperature stable TSPCD elements of a size of 3 per carat were 
coated with tungsten metal to a thickness of about 6 microns. The powder 
used to form the matrix carrier was tungsten carbide powder of 3 to 5 
micron particle size. About 1,000 grams of this powder were completely and 
thoroughly mixed with a solution of 200 ml. of hexane in which 20 grams of 
paraffin and mineral oil had been dissolved. The resultant mixture was 
heated to between 80 to 100 degrees C. for 45 minutes to evaporate the 
hexane completely. The processed powder was then ball milled, as 
described, for thirty minutes to break up the flocculated powder and then 
screened through a 200 mesh screen. 
The tungsten coated TSPCD elements were arranged in a suitable hexagonal 
die and 4.5 grams of the processed tungsten carbide powder was placed in 
the mold to fill the space between the TSPCD elements and to cover them. 
The resulting assembly was then cold pressed at 20,000 psi to form a 
hexagonal preform. 
The hexagonal preform was then loaded into a rubber mold which was then 
evacuated and sealed and then isostatically pressed at 29,000 psi. The 
resulting product was then ground to specific size. 
The isostatically processed hexagonal product was then placed on a crucible 
with 2.6 grams of a copper based alloy (Cu-Sn-Mn-Ni) on the powder side. 
The preform was then heated in a vacuum furnace (10 to the minus 5 torr) 
at the rate of 5 degrees C. per minute up to 400 degrees C. for one hour 
and then at 10 degrees C. per minute to a temperature of 1160 degrees C. 
for one hour for infiltration, later followed by cooling. 
Heating at a temperature over 1100 degrees C. for one hour is important 
because it is at this stage that tungsten carbide formation takes place. 
Typically the tungsten carbide layer thus formed is about 3 microns thick. 
If the preform is heated quickly to 1,000 degrees C. and held for 1.5 
hours, the formed tungsten carbide layer is about 0.3 microns thick. 
Heating to the carbide forming temperature at the rate of 10 degree C. per 
minute may also be used. 
After the thermal cycle, the finished product is surface ground to a 
thickness of about 0.315 of an inch and may be used. 
As a variant, cemented tungsten carbide grit (94% by weight of tungsten 
carbide bonded with 6% by weight of cobalt, a commercially available 
material) of 400 mesh size was mixed with a solution of 2% by weight 
paraffin in hexane. 
It is within the scope of this invention to form the isostatically pressed 
part and then process that part so that it is simulataneously bonded to a 
supporting structure such as a matrix bit body or other support structure 
while effecting conversion to the carbide layer described. For example, 
carburized tungsten powder in the nominal size range of 3 to 5 microns was 
ball milled with 1% by weight of nickel powder (325 mesh) for one hour. 
The milled powder mixture was then mixed with a solution of 2% by weight 
of paraffin wax in hexane. 
The mixture was dried by heating and then the processed powders were used 
with triangular TSPCD elements, coated as already described, to form a 
much larger assembly, as described. The larger assembly was cold axially 
pressed and then isostatically pressed as described. The resulting product 
was a "green" hexagonal cutter as shown in FIG. 2. The green assembly was 
then heated to burn off the organic material and held at a temperature of 
1,000 degrees C. for one hour. 
Thereafter, the processed green assembly, sufficiently strong to be handled 
was assembled to a matrix powder material in a mold, e.g. the matrix bit 
forming operation, and the matrix infiltrated at 1,200 degrees C. During 
the matrix infiltration, the green assembly was bonded to the matrix and 
the coating was formed into the carbide layer. In this processing there 
was a strong bond between the metal binder of the matrix and that in the 
green assembly and between the coating, powder and matrix supporting 
structure. Essentially the same processing may be used to form other 
products already described in or on a matrix carrier support element. 
Another form of one step infiltration involves the use of powders processed 
as follows: As received carburized tungsten carbide powder in a particle 
size range of from 3 to 5 microns was screened through a 200 mesh screen 
to break up the agglomerates which tend to form in the fine powder. The 
screened powders were mixed with 7 weight percent of nickel powder having 
a particle size in the range of 3 to 7 microns and mixed in a suitable 
mixer for one hour. A second tungsten carbide powder of a particle size in 
the range of 3 to 5 microns was screened through a 200 mesh screen to 
break of the larger agglomerates. The screened material was then ball 
milled with 3 weight percent of nickel powder of a particle size range of 
from 3 to 7 microns with 2 weight percent of paraffin in a hexane solution 
for about eight hours. The ball milled powders were then dried and coated 
with paraffin. 
Six pieces of tungsten coated triangular TSPCD elements, coated as already 
described, of a size of 3 per carat were arranged in a hexagonal punch and 
about 0.8 grams of the second powder was placed between the TSPCD 
elements, spaced as already described. About 4 grams of the first powder 
was then placed in the die and a hexagon product was formed under pressure 
of 15,000 psig. The cold pressed hexagonal product was then isostatically 
pressed at 29,000 psig. After isostatic pressing the hexagonal product was 
infiltrated directly into a matrix, such as a drill bit matrix using a 
copper-manganese-tin-nickel alloy. 
In another example, tungsten carbide powder in the size range of 20 to 30 
microns and in the range of 60 to 70 microns was ball milled with 3 weight 
percent of nickel powder, of the type and size described, with 2 weight 
percent of paraffin in a hexane solution. The powders were dried, screened 
through a 200 mesh screen, assembled to TSPCD elements as already 
described and cold pressed in the fixture. 
The cold pressed material with the TSPCD elements was then transferred to a 
high vacuum furnace, optionally a hydrogen furnace, to burn off the 
organic components by heating relatively slowly. This was accomplished by 
heating at a rate of about 5 degrees C. per minute to a temperature of 800 
degres C. The burned off hexagonal shapes were then assembled in a mold, 
and infiltrated into a matrix to provide a finished part, in this case a 
drill bit. 
It is to be understood that the one-step infiltration process described may 
be used to form any of a variety of products in accordance with this 
invention. 
In an alternate embodiment of the invention, the coated TSPCD elements may 
be bonded directly to the body of a tool matrix instead of to a matrix 
carrier which is in turn bonded to a tool matrix. In such a case, the 
steps of compacting the matrix powder by cold axial pressing and cold 
isostatic pressing are normally eliminated with the result that the matrix 
found after infiltration or sintering is not as dense as that obtained 
with the compacting steps. Such products are quite satisfactory, however, 
for products such as oil and gas drill and core bits and have important 
advantages in case of fabrication. 
The abrasive character of the products in accordance with the present 
invention may be enhanced somewhat by adding to the powder materials 
relatively small particles of diamond or TSPCD material in the form of 
particles having the approximate size of the powders used. The volume 
percent of such diamond powders may be as high as 40% and the resulting 
material is processed as already described with the bonding as already 
described. The starting diamond material is preferably synthetic 
polycrystalline diamond which is temperature stable although natural 
diamond material may also be used in some instances. 
It will be apparent to those skilled in the art that there may be 
variations and alterations, based on the above detailed disclosures, of 
the various procedures and product here described. It is to be considered 
that the same may come within the scope of the present invention as set 
forth in the appended claims.