US3779716A - Tantalum carbide-tantalum fiber composite material - Google Patents
Tantalum carbide-tantalum fiber composite material Download PDFInfo
- Publication number
- US3779716A US3779716A US00218686A US3779716DA US3779716A US 3779716 A US3779716 A US 3779716A US 00218686 A US00218686 A US 00218686A US 3779716D A US3779716D A US 3779716DA US 3779716 A US3779716 A US 3779716A
- Authority
- US
- United States
- Prior art keywords
- tac
- tantalum
- percent
- vol
- chopped
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Lifetime
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/64—Burning or sintering processes
- C04B35/645—Pressure sintering
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
- C04B35/56—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbides or oxycarbides
- C04B35/5607—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbides or oxycarbides based on refractory metal carbides
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/71—Ceramic products containing macroscopic reinforcing agents
- C04B35/74—Ceramic products containing macroscopic reinforcing agents containing shaped metallic materials
- C04B35/76—Fibres, filaments, whiskers, platelets, or the like
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/71—Ceramic products containing macroscopic reinforcing agents
- C04B35/78—Ceramic products containing macroscopic reinforcing agents containing non-metallic materials
- C04B35/80—Fibres, filaments, whiskers, platelets, or the like
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C49/00—Alloys containing metallic or non-metallic fibres or filaments
Definitions
- fracturing means the separation of a massive body into two or more smaller bodies.
- a chopped metal fiber to the refractory metal carbide will substantially enhance the thermal stress resistance of the carbide.
- the refractory metal carbide-metal fiber composites may readily be formed through hot pressing. While various refractory metal carbides may be used as the matrix material, it is desirable that the carbide be a monorather than a dicarbide.
- Various chopped metal fibers such as Ta, Mo, 75 vol percent W-25 vol percent Re, Re, etc., may be used. In particular, chopped rhenium fibers are useful because rhenium does not form a carbide.
- the limiting factor in the use of a particular metal fiber in the composites of this invention is the formation of the metal carbide-carbon eutectic. It will be apparent that the use of a metal fiber M as a reinforcing material in a metal carbide matrix is undesirable if the temperature of the MC-C eutectic is below that to which the composite will be exposed in its structural use. In the case of rhenium, the limiting temperature regime is that at which the Re-C eutectic occurs. The temperatures at which the various refractory metal carbides form eutectics with carbon are well known in the art.
- FIGURE compares the results of steady-state thermal stress testing of various TaC-chopped Ta wire specimens machined in both the parallel and perpendicular to the pressing direction with that ofa pure TaC specimen tested in the parallel direction only.
- Tantalum wire 20 mils in diameter was chopped to approximately 0.25 inch lengths and blended in desired proportions with TaC powder having 1.5 micron nominal size.
- the blended material was then hot pressed at l,800 C for a time sufficient to produce a density of about to percent theoretical. Typically, this took about onehalf hour.
- thermal shock data for these materials are summarized in Table I.
- two thermal shock indices are given; one pertains to crack initiation and one pertains to fracture. This latter index is more important in terms of the ultimate capability of these materials.
- Included in Table I for comparison are the results for with-grain RVC graphite. As can be seen, crack initiation was not obtained with RVC; rather fractures through the washer occur.
- the numbers refer to the volume percent TaC or Ta.
- As pressed means the composite prepared by hot pressing at l,800 C for about one-half hour.
- Heat treated means exposed to 2,300 C for 10 hours in a hydrogen environment after being hot pressed. It can be seen that the hot pressed composites show some slight reaction of the Ta fibers with the surrounding TaC matrix to produce the lesser carbide Ta C.
- the heat treated specimens having higher Ta fiber contents show a much more pronounced reaction between the fibers and the surrounding TaC matrix to produce Ta C.
- the strong presence of the hydride phase indicates that even after l0 hours at 2,300 C a substantial amount of the Ta remains noncarbided. It is not critical to this invention that the fibers remain substantially present as the metal.
- the lesser metal carbides have physical and mechanical properties that are sufiiciently different than those of the monocarbide matrix that crack propagation is stopped or greatly impeded on reaching them. They thus serve to prevent or greatly inhibit fracturing in substantially the same manner that the metal fibers do.
- a structural material having an improved thermal stress resistance at temperatures in excess of 2,000 C comprising a composite of 50 volume percent TaC and 50 volume percent chopped Ta fibers.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Ceramic Engineering (AREA)
- Materials Engineering (AREA)
- Organic Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Structural Engineering (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Inorganic Chemistry (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
Abstract
The thermal stress resistance of refractory metal carbides is substantially improved by the addition of chopped metal fibers. A composite consisting of 50 vol percent TaC-50 vol percent chopped Ta wire shows approximately a 40 percent improvement in thermal stress resistance over that of pure TaC.
Description
United States Patent [1 1 Riley et al.
[ TANTALUM CARBIDE-TANTALUM FIBER COMPOSITE MATERIAL [75] Inventors: Robert E. Riley; James M. Taub,
both of Los Alamos, N. Mex.
[73] Assignee: The United States of America as represented by the United States Atomic Energy Commission, Washington, DC.
22 Filed: Jan. 18,1972
211 Appl. No.: 218,686
[52] US. Cl. 29/l82.8, 75/204, 75/DIG. 1 [51] Int. Cl. C22c 29/00 [58] Field of Search 75/DIG. 1, 203, 204;
[56] References Cited UNlTED STATES PATENTS 11/1966 Jens 75/DIG. 1
[ Dec. 18, 1973 3,149,253 9/1964 Luebke 75/D1G. 1 3,479,155 11/1969 Rudy 29/1827 3,114,197 12/1963 De Bois et al. 75/D1G. 1 3,352,650 11/1967 Goldstein et al 75/D1G. 1
Primary Examiner-Carl D. Quarforth Assistant ExaminerE. A. Miller Att0rneyJ0hn A. Horan [57] ABSTRACT 1 Claim, 1 Drawing Figure TANTALUM CARBIDE-TANTALUM FIBER COMPOSITE MATERIAL BACKGROUND OF THE INVENTION The invention described herein was made in the course of, or under, a contract with the U. S. ATOMIC ENERGY COMMISSION. It relates to structural materials having improved thermal stress resistance at temperatures in excess of 2,000 C and more particularly to such materials consisting of refractory metal carbide-refractory metal fiber composites.
It is known in the art that structural materials exposed to temperatures in excess of 2,500 C for any substantial period of time, i.e., for more than 60 minutes, rapidly degrade. Refractory metal carbides are obvious candidates for such structural materials. However, they are brittle and readily crack in such temperature regimes. This cracking in turn rapidly leads to complete fracturing which may result in a catastrophic failure of the particular structure. As used within this application, fracturing means the separation of a massive body into two or more smaller bodies.
SUMMARY OF THE INVENTION We have now found that the addition of a chopped metal fiber to the refractory metal carbide will substantially enhance the thermal stress resistance of the carbide. The refractory metal carbide-metal fiber composites may readily be formed through hot pressing. While various refractory metal carbides may be used as the matrix material, it is desirable that the carbide be a monorather than a dicarbide. Various chopped metal fibers such as Ta, Mo, 75 vol percent W-25 vol percent Re, Re, etc., may be used. In particular, chopped rhenium fibers are useful because rhenium does not form a carbide. The limiting factor in the use of a particular metal fiber in the composites of this invention is the formation of the metal carbide-carbon eutectic. It will be apparent that the use of a metal fiber M as a reinforcing material in a metal carbide matrix is undesirable if the temperature of the MC-C eutectic is below that to which the composite will be exposed in its structural use. In the case of rhenium, the limiting temperature regime is that at which the Re-C eutectic occurs. The temperatures at which the various refractory metal carbides form eutectics with carbon are well known in the art.
We have found that a composite consisting of 50 vol percent TaC-50 vol percent chopped Ta wire shows approximately a 40 percent improvement in thermal stress resistance over that of pure TaC. At temperatures in excess of 2,500 C, a composite material of this type will still crack, but the presence of the fibers inhibits the propagation of the cracks completely through the structure so that fracturing is avoided or substantially reduced. As can be seen from the FIGURE, up to about 70 vol percent Ta, TaC-chopped Ta wire composite materials exhibit isotropic thermal characteristics. This indicates that neither the size nor the diameter to length ratio of the chopped metal fibers is critical in the composites of this invention. Indeed, it suggests that the metal need not be present as fibers at all but may serve as well in an irregular particulate form.
BRIEF DESCRIPTION OF THE DRAWING The FIGURE compares the results of steady-state thermal stress testing of various TaC-chopped Ta wire specimens machined in both the parallel and perpendicular to the pressing direction with that ofa pure TaC specimen tested in the parallel direction only.
DESCRIPTION OF THE PREFERRED EMBODIMENT Tantalum wire 20 mils in diameter was chopped to approximately 0.25 inch lengths and blended in desired proportions with TaC powder having 1.5 micron nominal size. The blended material was then hot pressed at l,800 C for a time sufficient to produce a density of about to percent theoretical. Typically, this took about onehalf hour.
Steady-state thermal stress specimens were machined from the 10, 50, 60, and 70 vol percent Ta wire billets in both the parallel and perpendicular to the pressing direction. The FIGURE compares the results of steadystate thermal stress testing on these materials with that of pure TaC specimen tested in the parallel direction only. The percent TaC material was 96 percent of theoretical density. There is clearly a significant increase in thermal stress resistance associated with certain contents of Ta fiber. With the exception of the 30 vol percent TaC-70 vol percent specimens, the material is isotropic. Whereas pure refractory metal carbides have steady-state thermal stress resistances in the range of 500 to 650 C radiator temperature, the 50 vol percent TaC-50 vol percent chopped Ta wire composite material has a steady thermal stress resistance at about 900 C radiator temperature. This is an improvement of about 40 percent over that of TaC alone.
One-inch-o.d. by one-quarter-inch-i.d. by one sixteenth-inch-thick specimens of TaC reinforced with 60 and 70 vol percent chopped Ta wire were thermally shock tested. There was a large difference in the power setting required to initiate a crack and the power setting required to completely fracture the materials. Typ ically, a crack could be made to initiate at a power setting of 801l0 and then to propagate (sometimes across the entire specimen). However, these cracks were very tight and did not significantly degrade the strength of the specimen. Apparently the Ta wires bridging the cracks act in effect as tiny reinforcing bars. With the thermal shock instrumentation used, pure refractory metal carbides require power settings of 60 to 80 for crack initiation. In such carbides, however, only a slight increase in the power setting leads to rapid fracture.
It was only at power settings in excess of 200 that these materials could be fractured. In fact, the withgrain specimens could not be fractured at all, even though, at these power settings, the specimens had so many cracks that they resembled cracked safety glass. Several specimens were finally forced to part into two pieces by melting the Ta wires holding the cracked segments together.
The thermal shock data for these materials are summarized in Table I. As can be seen, two thermal shock indices are given; one pertains to crack initiation and one pertains to fracture. This latter index is more important in terms of the ultimate capability of these materials. Included in Table I for comparison are the results for with-grain RVC graphite. As can be seen, crack initiation was not obtained with RVC; rather fractures through the washer occur.
Room temperature comparative thermal conductivity data were also obtained on these materials. Table II presents a comparison between the experimental and predicted values of the thermal conductivity. The model assumed is a dispersion of Ta wires in a continuous matrix of TaC. The axes of the wires are assumed to be parallel to the radial plane of the pressing, but randomly oriented in that plane. The porosity relationships were those derived for hot-pressed ZrC.
Table I THERMAL SHOCK DATA FOR Ta WIRE REINFORCED TaC COMPOSITES Thermal Shock Index Grain For Crack Material Orientation Initiation For Fracture RVC Graphite 252/255 60 vol Ta wire 40 vol TaC WG 80/100 can't fracture 60 vol Ta wire 40 vol TaC AG 70/80 225 70 vol Ta wire 30 vol TaC WG 80/!00 cant fracture* 70 vol Ta wire 30 vol TaC AG 60/80 200 3 *Melting of Ta fibers occurs before fracture Table II COMPARISON OF PREDICTED AND EXPERIMETAL VALUES OF THERMAL CONDUCTIVITY OF TaC-Ta (WIRE) HOT-PRESSED COMPOSITE BODIES (W/cmK at Table III shows x-ray diffraction data for various TaC-chopped Ta wire composites. The numbers refer to the volume percent TaC or Ta. As pressed means the composite prepared by hot pressing at l,800 C for about one-half hour. Heat treated means exposed to 2,300 C for 10 hours in a hydrogen environment after being hot pressed. It can be seen that the hot pressed composites show some slight reaction of the Ta fibers with the surrounding TaC matrix to produce the lesser carbide Ta C. The heat treated specimens having higher Ta fiber contents show a much more pronounced reaction between the fibers and the surrounding TaC matrix to produce Ta C. The strong presence of the hydride phase indicates that even after l0 hours at 2,300 C a substantial amount of the Ta remains noncarbided. It is not critical to this invention that the fibers remain substantially present as the metal. The lesser metal carbides have physical and mechanical properties that are sufiiciently different than those of the monocarbide matrix that crack propagation is stopped or greatly impeded on reaching them. They thus serve to prevent or greatly inhibit fracturing in substantially the same manner that the metal fibers do.
TABLE III X-RAY DIFFRACTION DATA FOR TaC-CHOPPED Ta WIRE COMPOSITES Phases Present Sample Description Strong Medium Weak 90 TaC-l0 Ta as pressed TaC Ta C TaC-3O Ta as pressed TaC Ta C 50 TaC-50 Ta as pressed TaC Ta,C 40 TaC-60 Ta as pressed TaC Ta C 30 TaC-70 Ta as pressed TaC Ta,C TaC-l0 Ta heat-treated TaC 70 TaC-30 Ta heat-treated TaC Ta C 50 TaC-50 Ta heat-treated Ta C TaH TaC 4O TaC-60 Ta heat-treated Ta,C
TaC
o.1\ 30 TaC-7O Ta heat-treated Ta C TaC TaH
What we claim is:
I. A structural material having an improved thermal stress resistance at temperatures in excess of 2,000 C comprising a composite of 50 volume percent TaC and 50 volume percent chopped Ta fibers.
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US21868672A | 1972-01-18 | 1972-01-18 |
Publications (1)
Publication Number | Publication Date |
---|---|
US3779716A true US3779716A (en) | 1973-12-18 |
Family
ID=22816077
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US00218686A Expired - Lifetime US3779716A (en) | 1972-01-18 | 1972-01-18 | Tantalum carbide-tantalum fiber composite material |
Country Status (1)
Country | Link |
---|---|
US (1) | US3779716A (en) |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4067742A (en) * | 1976-04-01 | 1978-01-10 | Nasa | Thermal shock and erosion resistant tantalum carbide ceramic material |
US4300951A (en) * | 1978-02-24 | 1981-11-17 | Kabushiki Kaisha Fujikoshi | Liquid phase sintered dense composite bodies and method for producing the same |
US4555268A (en) * | 1984-12-18 | 1985-11-26 | Cabot Corporation | Method for improving handling properties of a flaked tantalum powder composition |
Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US3114197A (en) * | 1960-06-17 | 1963-12-17 | Bendix Corp | Brake element having metal fiber reinforcing |
US3149253A (en) * | 1962-01-03 | 1964-09-15 | Gen Electric | Electrode structure from magnetohydrodynamic device |
US3285825A (en) * | 1964-09-16 | 1966-11-15 | Atomic Power Dev Ass Inc | Reinforced ceramic fuel elements |
US3352650A (en) * | 1965-07-19 | 1967-11-14 | Goldstein David | Metallic composites |
US3479155A (en) * | 1962-11-20 | 1969-11-18 | Schwarzkopf Dev Co | Heat-shock resistant shaped high temperature metal ceramic bodies |
-
1972
- 1972-01-18 US US00218686A patent/US3779716A/en not_active Expired - Lifetime
Patent Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US3114197A (en) * | 1960-06-17 | 1963-12-17 | Bendix Corp | Brake element having metal fiber reinforcing |
US3149253A (en) * | 1962-01-03 | 1964-09-15 | Gen Electric | Electrode structure from magnetohydrodynamic device |
US3479155A (en) * | 1962-11-20 | 1969-11-18 | Schwarzkopf Dev Co | Heat-shock resistant shaped high temperature metal ceramic bodies |
US3285825A (en) * | 1964-09-16 | 1966-11-15 | Atomic Power Dev Ass Inc | Reinforced ceramic fuel elements |
US3352650A (en) * | 1965-07-19 | 1967-11-14 | Goldstein David | Metallic composites |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4067742A (en) * | 1976-04-01 | 1978-01-10 | Nasa | Thermal shock and erosion resistant tantalum carbide ceramic material |
US4300951A (en) * | 1978-02-24 | 1981-11-17 | Kabushiki Kaisha Fujikoshi | Liquid phase sintered dense composite bodies and method for producing the same |
US4555268A (en) * | 1984-12-18 | 1985-11-26 | Cabot Corporation | Method for improving handling properties of a flaked tantalum powder composition |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
US3084421A (en) | Reinforced metallic composites | |
Burakovsky et al. | Ab initio phase diagram of iridium | |
Kalish et al. | Densification mechanisms in high‐pressure hot‐pressing of HfB2 | |
CN109898005A (en) | A kind of WVTaZrHf infusibility high-entropy alloy of high intensity and preparation method thereof | |
Jones et al. | Fusion reactor application issues for low activation SiC/SiC composites | |
US3779716A (en) | Tantalum carbide-tantalum fiber composite material | |
Kreider et al. | Thermal expansion of boron fiber-aluminum composites | |
US3214833A (en) | Ceramic to metal bonding process | |
US3325300A (en) | Refractory bodies and compositions and methods of making the same | |
Peterson et al. | Properties of thorium, its alloys, and its compounds | |
US4304870A (en) | Ablative-resistant dielectric ceramic articles | |
US3460920A (en) | Filament reinforced metal composites for gas turbine blades | |
Sarian | Elevated temperature stability of carbon-fibre, nickel-matrix composites: morphological and mechanical property degradation | |
Kantan et al. | Sintering of thorium and thoria | |
Riley et al. | Improved thermal-shock-resistant carbides | |
Helm | Radiation-effects in graphite at high temperature | |
Diefendorf et al. | PYROLYTIC GRAPHITES HOW STRUCTURE AFFECTS PROPERTIES | |
US2888343A (en) | Alloys and members produced therefrom | |
Kovbashyn et al. | The study of technological peculiarities for improvement of chemical and physico-mechanical properties of reaction-sintered ceramic materials based on molybdenum disilicide | |
US3362817A (en) | Bonding composition for integrally joining carbonaceous products to each other and to metals | |
Carbides | c3q | |
Hughel | An Investigation of the Precision Mechanical Properties of Several Types of Beryllium | |
Page et al. | Evaluation of zirconia, thoria and zirconium diboride for advanced resistojet use | |
Harada | Graphite-metal Composites Quarterly Report No. 3, Feb. 1-May 1, 1966 | |
Bortz et al. | Properties of tantalum carbide-graphite and niobium carbide-graphite composites |