EP0083580A1 - High damping epoxy resin composite - Google Patents

High damping epoxy resin composite

Info

Publication number
EP0083580A1
EP0083580A1 EP19810902134 EP81902134A EP0083580A1 EP 0083580 A1 EP0083580 A1 EP 0083580A1 EP 19810902134 EP19810902134 EP 19810902134 EP 81902134 A EP81902134 A EP 81902134A EP 0083580 A1 EP0083580 A1 EP 0083580A1
Authority
EP
European Patent Office
Prior art keywords
weight
epoxy
damping
composite
modulus
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.)
Withdrawn
Application number
EP19810902134
Other languages
German (de)
French (fr)
Inventor
Daniel A. Scola
Marvin C. Cheney, Jr.
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Raytheon Technologies Corp
Original Assignee
United Technologies Corp
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by United Technologies Corp filed Critical United Technologies Corp
Publication of EP0083580A1 publication Critical patent/EP0083580A1/en
Withdrawn legal-status Critical Current

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08G—MACROMOLECULAR COMPOUNDS OBTAINED OTHERWISE THAN BY REACTIONS ONLY INVOLVING UNSATURATED CARBON-TO-CARBON BONDS
    • C08G59/00—Polycondensates containing more than one epoxy group per molecule; Macromolecules obtained by polymerising compounds containing more than one epoxy group per molecule using curing agents or catalysts which react with the epoxy groups
    • C08G59/18—Macromolecules obtained by polymerising compounds containing more than one epoxy group per molecule using curing agents or catalysts which react with the epoxy groups ; e.g. general methods of curing
    • C08G59/20—Macromolecules obtained by polymerising compounds containing more than one epoxy group per molecule using curing agents or catalysts which react with the epoxy groups ; e.g. general methods of curing characterised by the epoxy compounds used
    • C08G59/22—Di-epoxy compounds
    • C08G59/226—Mixtures of di-epoxy compounds
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08K—Use of inorganic or non-macromolecular organic substances as compounding ingredients
    • C08K7/00—Use of ingredients characterised by shape
    • C08K7/02—Fibres or whiskers

Definitions

  • the field of art to which the invention pertains is mixed epoxy resin compositions and fiber containing composites made therefrom.
  • the present invention is directed to an epoxy resin, composite with high damping, high strength and high modulus of elasticity properties.
  • the resin component comprises about 12% to about 35% by weight of a high stiffness epxoy resin in admixture with about 20% to about 43% by weight of a flexible epoxy resin and about 35% to about 61% by weight of a flexibilizing curing agent.
  • a composite of such resin in admixture with about 20% to about 50% reinforcing fibers results in a high damping, high strength and high modulus composite.
  • Fig. 1 demonstrates a comparison of damping curves of conventional carbon-epoxy composites with carbon-epoxy composites of the present invention
  • Figs. 2, 3, 4 , 5, 6 and 7 compare the damping curves of composites of the present invention based on different percents of the components, with and without tip weights;
  • Fig. 8 demonstrates the relationship of damping to shear modulus and flexure modulus of composites of the present invention.
  • Fig. 9 demonstrates graphically a comparison of damping values of conventional composites and those of the present invention.
  • the main components of . the " high damping composites of the present invention are the admixture of a flexible long chain aliphatic epoxy component with a standard bisphenol-A stiff epxoy resin, and a flexible long chain amine fatty acid amide curing agent, blended in specific percentage ranges.
  • n 0, 1 or 2 (G.P.C. determined molecular weights of 340, 608 and 876 respectively).
  • the stiff epoxy component is a diglycidyl ester linoleic dimer acid such as Epon 871 with the structural
  • the curing agent is a flexible cross-linking agent which is a long chain a ine fatty acid amide such as Versamid V-40 (General Mills) .
  • the flexible epoxy (such as Epon 828) is used in a range of from about 20% to about 43% by weight and preferably about 27% by weight
  • the stiff epoxy (such as Epon 871) is used in a range of about 12% to about 35% by weight and preferably about 27% by weight
  • the flexible curing agent (such as Versamid V-40) is used in a range of about 35% to about 61% and preferably about 49% by weight.
  • Composites were formulated by dissolving the resin formulation in a solvent such as methyl ethyl ketone to make an approximately 50% by weight solution.
  • Graphite fibers were preferably used in reinforcing the composites such as HMS (Hercules) and Thornel 75 (Union Carbide) of continuous tow. Fiber loading was about 20% to about 50% by weight based on weight of fiber plus resin composition, and preferably about 42% by weight.
  • the graphite fibers were directed by a pulley through the resin bath and wound onto a 17 inch (43.18 cm) diameter, 6 inch (15.24 cm) wide drum to produce a resin impregnated tape
  • OM ' approximately 4 inches (10.16 cm) wide for testing pur ⁇ poses.
  • the particular length and thickness of the tape can be varied depending on the ultimate use.
  • the solvent was evaporated from the tape at room temperature.
  • the tape was removed and cut into four 12 inch (30.48 cm) sections and cured to a B stage in an oven at approximately 80°C for approximately 15 minutes under vacuum.
  • the tapes were removed and cut into approximately 4 by 6 inch (10.16 by 15.24 cm) sections and laid one over the other in a mold for pro ⁇ duction of a multi-layered composite.
  • fiber laying can be in any desired orientation in the composite, uni ⁇ directional laying is preferred for flexbeam uses, for example, and cross-ply laying (e.g., 0°, 45°, 90°; 0°, 30°, 60°; 0°, 90°; etc.) for other uses such as acoustical or spar uses.
  • the mold was placed in a preheated press at about 100°C and a constant pressure of approximately 200 psi .(1.33 x 10 NT/M ) for 10 minutes was imposed followed by curing under this pressure at 100°C for approximately one hour.
  • the molded composite was then post-cured for one hour at approximately 125°C.
  • Epon 828 50 40 75 75 60 60 50 50
  • the specimens were instrumented between the inner two-load points and the strain recorded on a two-axes plot.
  • the specimens were loaded to failure as indicated by complete physical separation or by large excursions and strain. Flexural tests were made for two samples of each composite and the results averaged.' The moduli were determined from the initial slope of the stress- strain curves. In some cases, particularly for the higher damping samples such as 1, 4 and 9, the curve became non ⁇ linear significantly prior to failure and thus the values of modulus given in Table III for these specimens are somewhat misleading. Nominal values of approximately 75% of those listed will be more realistic for preliminary design purposes. It should also be noted that the flexure modulus determined from four-point loading tests corre ⁇ lates well with axia tests.
  • point loading placed the specimens under shear deformation and thus, would be influenced to a greater extent by the properties (e.g. modulus) of the matrix.
  • properties e.g. modulus
  • four-point tests have produced modulus values as much as 50% higher than those from cantilevered tests. This difference, of course, is less for composites with high modulus resins. This accounts in part for the apparent inconsistencies in comparing flexure modulus of the various specimens and then comparing the corresponding torsion modulus. The percent differences in the torsional properties are generally much larger due to the above reason.
  • the shear properties were determined using a simple torsional loading fixture and manually loading cantilever specimens in torsion measuring the tip angular deflection and calculating the modulus from the formula
  • a tip weight of 76 g s was added in some cases as indicated on the Figures.
  • the tip weight clamp was securely affixed to avoid looseness but not so tight as to prevent shear deformation at the free end. Some reduction in the free end shear probably occurred which would tend to add stiffness and reduce damping; however, no estimate was made.
  • the specimen length of six inches (15.24 cm) was not maintained pre ⁇ cisely which would account for some minor differences in frequency. Variations in this dimension were less than i ⁇ .1 inch ( ⁇ 2.54 cm) for all specimens except 9 and 10. For these cases, the specimen length was approximately 7.5 inches (19.05 cm). Damping levels were calculated by comparing response amplitudes at two adjacent peaks and substituting in the equation for damping ratio:
  • Figure 9 compares the system stability of a heli ⁇ copter wind tunnel model using a high damping rotor according to the present invention (curve A) with that of a conventional or low damping rotor (curve B) . As can be seen from the tests, the blade system according to the present invention never really went unstable.
  • composites of the present invention have the following properties: flexural strength greater than 5 x 10 3 psi (3.5 x 10 7 NT M 2 ), and preferably greater than 15 x 10 3 psi (1.03 x 10 8 NT/M 2 ); flexural modulus greater than 10 x 10 psi (6.9 x 10 NT/M ) and preferably greater than 14 x 10 6 psi (9.7 x 10 10 NT/M 2 ); damping up to about 3% critical and preferably up to about
  • damping levels do not appear to be affected by the addition of a concentrated mass, response frequency, or response amplitude, however, note the test in a rotating environment discussed above.
  • the low shear modulus of these materials would allow significant reduction in flexbeam length.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Health & Medical Sciences (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Medicinal Chemistry (AREA)
  • Polymers & Plastics (AREA)
  • Organic Chemistry (AREA)
  • Compositions Of Macromolecular Compounds (AREA)
  • Vibration Prevention Devices (AREA)

Abstract

Un matériau composite à base de résine époxy possède des propriétés améliorées d'amortissement ainsi qu'une bonne résistance et un module d'élasticité élevé. La composition comprend une résine époxyde telle qu'une résine époxyde d'éther épichlorohydrine-bisphénol-A-diglycide mélangée avec une résine époxyde flexible telle qu'une résine époxyde d'ester glycidyle d'acide dimère linoléique et un agent de réticulation flexible tel qu'une amide d'acide gras-amine à chaîne longue. La composition mélangée avec des fibres ayant un module d'élasticité élevé telles que des fibres de graphite forme des matériaux composites ayant des propriétés améliorées d'amortissement, une bonne résistance et un module d'élasticité élevé. Des utilisations caractéristiques des matériaux composites de la présente invention sont des poutres de flexions pour des rotors sans articulation et sans palier et pour des matériaux de barrière acoustique.A composite material based on epoxy resin has improved damping properties as well as good resistance and a high elastic modulus. The composition comprises an epoxy resin such as an epichlorohydrin-bisphenol-A-diglycide ether epoxy resin mixed with a flexible epoxy resin such as a linoleic dimeric acid glycidyl ester epoxy resin and a flexible crosslinking agent such than a long chain fatty acid amine amide. The composition mixed with fibers having a high modulus of elasticity such as graphite fibers forms composite materials having improved damping properties, good strength and a high modulus of elasticity. Typical uses of the composite materials of the present invention are flexural beams for rotors without articulation and without bearings and for acoustic barrier materials.

Description

Description
High Damping Epoxy Resin Composite
Technical Field
The field of art to which the invention pertains is mixed epoxy resin compositions and fiber containing composites made therefrom.
Background Art
While the prior art has considered various resin mixtures for various purposes, a high damping resin compo- sition with good strength and modulus of elasticity properties is not available. For example, while U. S. Patents 3,518,221; 3,598,693; 3,658,748; and 3,923,571 all teach epoxy resin composition mixtures including cross-linking agents, none recognize or address the prob- lem of high damping properties. Similarly, while these same references teach additions of various fibrous filler material (3,923,571 excluded), none contemplate high damping composites so constituted.
Disclosure of Invention The present invention is directed to an epoxy resin, composite with high damping, high strength and high modulus of elasticity properties. The resin component comprises about 12% to about 35% by weight of a high stiffness epxoy resin in admixture with about 20% to about 43% by weight of a flexible epoxy resin and about 35% to about 61% by weight of a flexibilizing curing agent. A composite of such resin in admixture with about 20% to about 50% reinforcing fibers results in a high damping, high strength and high modulus composite. Brief Description of the Drawings
Fig. 1 demonstrates a comparison of damping curves of conventional carbon-epoxy composites with carbon-epoxy composites of the present invention;
Figs. 2, 3, 4 , 5, 6 and 7 compare the damping curves of composites of the present invention based on different percents of the components, with and without tip weights;
Fig. 8 demonstrates the relationship of damping to shear modulus and flexure modulus of composites of the present invention; and
Fig. 9 demonstrates graphically a comparison of damping values of conventional composites and those of the present invention.
Best Mode for Carrying Out the Invention The main components of .the" high damping composites of the present invention are the admixture of a flexible long chain aliphatic epoxy component with a standard bisphenol-A stiff epxoy resin, and a flexible long chain amine fatty acid amide curing agent, blended in specific percentage ranges.
As the flexible epoxy an epichlorohydrin-bisphenol A diglycidyl ether epoxy is used such as Epon 828. Struc¬ turally, this is shown as follows:
where n = 0, 1 or 2 (G.P.C. determined molecular weights of 340, 608 and 876 respectively).
The stiff epoxy component is a diglycidyl ester linoleic dimer acid such as Epon 871 with the structural
O WI formula as follows :
The curing agent is a flexible cross-linking agent which is a long chain a ine fatty acid amide such as Versamid V-40 (General Mills) .
In order to obtain the improved damping, strength and modulus properties of the composites of the present invention, these materials must be used in a specific percentage range. The flexible epoxy (such as Epon 828) is used in a range of from about 20% to about 43% by weight and preferably about 27% by weight, the stiff epoxy (such as Epon 871) is used in a range of about 12% to about 35% by weight and preferably about 27% by weight, and the flexible curing agent (such as Versamid V-40) is used in a range of about 35% to about 61% and preferably about 49% by weight.
Composites were formulated by dissolving the resin formulation in a solvent such as methyl ethyl ketone to make an approximately 50% by weight solution. Graphite fibers were preferably used in reinforcing the composites such as HMS (Hercules) and Thornel 75 (Union Carbide) of continuous tow. Fiber loading was about 20% to about 50% by weight based on weight of fiber plus resin composition, and preferably about 42% by weight. The graphite fibers were directed by a pulley through the resin bath and wound onto a 17 inch (43.18 cm) diameter, 6 inch (15.24 cm) wide drum to produce a resin impregnated tape
OM ' ~ approximately 4 inches (10.16 cm) wide for testing pur¬ poses. The particular length and thickness of the tape can be varied depending on the ultimate use. After appli¬ cation to the drum the solvent was evaporated from the tape at room temperature. The tape was removed and cut into four 12 inch (30.48 cm) sections and cured to a B stage in an oven at approximately 80°C for approximately 15 minutes under vacuum. The tapes were removed and cut into approximately 4 by 6 inch (10.16 by 15.24 cm) sections and laid one over the other in a mold for pro¬ duction of a multi-layered composite. While fiber laying can be in any desired orientation in the composite, uni¬ directional laying is preferred for flexbeam uses, for example, and cross-ply laying (e.g., 0°, 45°, 90°; 0°, 30°, 60°; 0°, 90°; etc.) for other uses such as acoustical or spar uses. The mold was placed in a preheated press at about 100°C and a constant pressure of approximately 200 psi .(1.33 x 10 NT/M ) for 10 minutes was imposed followed by curing under this pressure at 100°C for approximately one hour. The molded composite was then post-cured for one hour at approximately 125°C. After removal from the mold, the composite was cut into appro¬ priate sample size shapes for physical, mechanical, and damping tests. Sample formulations are demonstrated by Tale I and physical property measurements by Table II. While the composites of the present invention can be formed in any desired shape, depending on their use, square and rectangular cross-section composites are pre¬ ferred, especially for flexbeam use, because of their ease of fabrication and particular high damping properties.
O P TABLE I Flexible Epoxy Resin Compositions
Material Formulation (wt.. gm)
A B C D E F G H
Epon 828 50 40 75 75 60 60 50 50
Epon 871 50 60 25 40 40 40 45 40
Versamid V-40 90 100 100 75 90 80 92 90
The composites were tested statically on a universal testing machine using a four-point loading technique to measure flexure properties. The results are shown in Table III.
The specimens were instrumented between the inner two-load points and the strain recorded on a two-axes plot. The specimens were loaded to failure as indicated by complete physical separation or by large excursions and strain. Flexural tests were made for two samples of each composite and the results averaged.' The moduli were determined from the initial slope of the stress- strain curves. In some cases, particularly for the higher damping samples such as 1, 4 and 9, the curve became non¬ linear significantly prior to failure and thus the values of modulus given in Table III for these specimens are somewhat misleading. Nominal values of approximately 75% of those listed will be more realistic for preliminary design purposes. It should also be noted that the flexure modulus determined from four-point loading tests corre¬ lates well with axia tests. However, it is found to be considerably higher than that determined from three-point and cantilevered tests. This difference is caused by the influence the matrix has in carrying load. Axial and four-point loading does not subject the specimen to shear deformation and therefore, the fibers have the major influence on modulus. Conversely, cantilever and thrree-
OMP
TABLE II
Some Physical Properties of High Damping Graphlte/Epoxy Conn;loaite
Graphite Vol. % Density
Sample No. Resin Form Fiber Type Fiber Resin Void gm/cc Piles Thickness in.
1 A IIMS 18.7 68.4 12.9 1.21 7 0.200
2 A Thornel 75 — — — — 16 0.124
3 C Thornel 75 31.9 63.4 4.8 1.36 16 0.142
4 D Thornel 75 29.7 59.6 10.7 1.28 15 0.137
5 D Thornel 75 28.7 62.2 9.18 1.29 16 0.138
6 E Thornel 75 31.9 58.9 9.2 1.31 16 0.137
72 H Thornel 75 45 55 — 1.70 22 0.137
2 8 F Thornel 75 40 60 — 1.50 21 0.155
92 ■ G Thornel 75 42 58 — 1.55 22 0.155
101' 2 G Thornel 75 42 58 — 1.55 22 0.155
An additional cure cycle was used on a portion of composite No. 9 to yield No. 10. The additional cure was 2 hours at 150°C. .
"The physical properties for these composites are estimated values.
TABLE III Mechanical and Damping Properties of High Damping Graphi e/Epoxy Composites
Torsional She
Flexural Properties Properties
Stre
Strength Modulus Bending Frequency, cps Damping, % Critical Modulus Elas
Sample No. 103 psi 106 pel /o tip wt w/tip wt w/o tip wt w/tip wt pel Limi 1 340 53 4.40 5.45 <5.8xl03 <7 2 26.77 23.3 313 1.77 — l.OxlO5 s
3 42.89 22.9 378 53 1.21 1.17 1.31x θ5 =6
4 6.45 12.5 336 5.12 — <1.03xl04 <1
5 49.6 21.8 385 55 . 0.87 0.90 2.11xl05 >1
6 33.47 21.1 373 52 1.15 1.19 l.OlxlO5 -4
7 24.12 24.8 — — 1.82xl05 6
8 39.1 27.6 — — 2.49xl05 >1
9 15.6 14.3 244 2.64 — <3.88x10* <9
10 18.14 16.4 238 1.3 — l.lOxlO5 3
or the stress at which nonlinear behavior was observed.
4-point, S/D •=■ 20/1. Average of two measurements.
point loading placed the specimens under shear deformation and thus, would be influenced to a greater extent by the properties (e.g. modulus) of the matrix. Previous results have shown that four-point tests have produced modulus values as much as 50% higher than those from cantilevered tests. This difference, of course, is less for composites with high modulus resins. This accounts in part for the apparent inconsistencies in comparing flexure modulus of the various specimens and then comparing the corresponding torsion modulus. The percent differences in the torsional properties are generally much larger due to the above reason.
The shear properties were determined using a simple torsional loading fixture and manually loading cantilever specimens in torsion measuring the tip angular deflection and calculating the modulus from the formula
Q
G -- θ'j where Q is the applied torque, θ' the twist rate, and J the polar moment of inertia for the high damping speci- mens. The loading fixture was not sufficiently sensitive to accurately measure torsion since the weight pans them¬ selves often cause the specimen to creep. For these cases, estimates were made as noted in Table III. Damping measurements were made using six-inch (15.24 cm) samples supported at one end. The samples were excited at their natural frequencies by striking them at the free end. The strain was measured at the root end and recorded on a Techtronics Dual Beam Storage Oscilliscope. The response curves are shown in Figures 2-7. The frequencies and damping levels were measured directly from these curves. A tip weight of 76 g s was added in some cases as indicated on the Figures. The tip weight clamp was securely affixed to avoid looseness but not so tight as to prevent shear deformation at the free end. Some reduction in the free end shear probably occurred which would tend to add stiffness and reduce damping; however, no estimate was made. The specimen length of six inches (15.24 cm) was not maintained pre¬ cisely which would account for some minor differences in frequency. Variations in this dimension were less than iθ.1 inch (±2.54 cm) for all specimens except 9 and 10. For these cases, the specimen length was approximately 7.5 inches (19.05 cm). Damping levels were calculated by comparing response amplitudes at two adjacent peaks and substituting in the equation for damping ratio:
where C = actual damping; C = critical damping; ό* = log represent the dimensions of the two adjacent peaks.
Damping levels were checked at various points to determine the effect of amplitude on damping and although the results showed some difference, no general trend was indicated. Also, the effect of tip weight did not indi- cate a consistent trend in its effect on damping. The results of the damping and modulus measurements are summarized in Fig. 8. The results on this Fig. should be viewed as qualitative since the moduli were different to define for the higher damping specimens. Attention should also be directed to Figures 1 and 9 for a comparison of conventional graphite/epoxy material (e.g., Canadian Patent 951,301) and the high damping material of the present invention and Fig. 9 when used in a matched stiffness composite bearingless rotor utilizing identical conditions and frequencies to compare stability characteristics under resonant conditions.
Figure 9 compares the system stability of a heli¬ copter wind tunnel model using a high damping rotor according to the present invention (curve A) with that of a conventional or low damping rotor (curve B) . As can be seen from the tests, the blade system according to the present invention never really went unstable.
As evidenced by Table III composites of the present invention have the following properties: flexural strength greater than 5 x 103 psi (3.5 x 107 NT M2), and preferably greater than 15 x 103 psi (1.03 x 108 NT/M2); flexural modulus greater than 10 x 10 psi (6.9 x 10 NT/M ) and preferably greater than 14 x 106 psi (9.7 x 1010 NT/M2); damping up to about 3% critical and preferably up to about
6% critical; torsional shear modulus less than about
3 x 10 5 and preferably less than about 4 x 104; and stress at elastic limit greater that 60 psi (4.1 x 105 NT/M )
5 2 and preferably greater than 90 psi (6.2 x 10 NT/M ). Accordingly, it has been demonstrated that epoxy composites of the composition and percents specified have - high internal damping. These damping levels can be con¬ trolled in this range chemically and through curing cycles as recited producing damping up to about 6% critical. The material at the high end of the range is generally unacceptable from the standpoint of stiffness and strength but the mid-range damping composites (e.g., sample No. 9 with a 2.64% damping) shows promise as a composite bearingless rotor flexbeam material for low edgewise stiffness designs. The damping levels do not appear to be affected by the addition of a concentrated mass, response frequency, or response amplitude, however, note the test in a rotating environment discussed above. In addition to the damping properties, the low shear modulus of these materials would allow significant reduction in flexbeam length.
Although this invention has been shown and described with respect to a preferred embodiment, it will be under¬ stood by those skilled in this art that various changes in form and detail thereof may be made without departing from the spirit and scope of the claimed invention.
OM

Claims

Claims
1. A high damping, high strength, high modulus composite comprising:
(a) a resin matrix comprising about 20% to about 43% by weight flexible epoxy, about 12% to about 35% by weight stiff epoxy, about 35% to about 61% by weight flexible curing agent, and
(b) about 20% to about 50% by weight of a high modulus fiber based on the weight of fiber plus resin.
2. The composite of claim 1 wherein the stiff epoxy is present in an amount about 24% by weight, the flexible epoxy is present in an amount about 27% by weight, and the flexible curing agent is present in an amount about 49% by weight.
3. The composite of claim 2 wherein the fiber is .present in an amount about 42% by weight.
4. The composite of claims 1, 2 or 3 wherein the flexi¬ ble epoxy is a linoleic dimer acid glycidal ester epoxy, the stiff epoxy is an epichlorohydrin-bisphenol-A-digly- cidal ether epoxy, the flexible cross-linking agent is a long chain amine-fatty acid amide, and the high modulus fiber is graphite.
5. The composite of claim 1 having a flexural strength greater than 5 x 103 psi (3.5 x 106 NT/M2), flexural modulus greater than 10 x 10 psi (6.9 x 1010 NT/M2), damping up to about 6% critical, torsional shear modulus less than about 3 x 10 , and stress at elastic limit greater than 60 psi (4.1 x 105 NT/M ) .
O wι 6. The composite of claim 1 having a flexural strength about 15.6 x 103 psi (10.8 x 107 NT/M2), flexural modulus about 14.3 x 106 psi (9.9 x 1010 NT/M2), damping about
2.64% critical, torsional shear modulus less than about 3.88 x 10 , and stress at elastic limit about 95 psi
(6. 6 x 105 NT/M2) .
EP19810902134 1981-07-13 1981-07-13 High damping epoxy resin composite Withdrawn EP0083580A1 (en)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/US1981/000945 WO1983000159A1 (en) 1981-07-13 1981-07-13 High damping epoxy resin composite

Publications (1)

Publication Number Publication Date
EP0083580A1 true EP0083580A1 (en) 1983-07-20

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Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5004764A (en) * 1988-02-12 1991-04-02 Mitsui Petrochemical Industries, Ltd. Composition for vibration damper, process for manufacture thereof, and vibration damper

Family Cites Families (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3445282A (en) * 1964-10-05 1969-05-20 Anaconda Wire & Cable Co Insulated electrical conductors and the method for producing the same
DE1593512C3 (en) * 1966-07-14 1974-09-19 Schering Ag, 1000 Berlin Und 4619 Bergkamen Process for the preparation of aliphatic glycidyl ethers
US3518221A (en) * 1967-10-30 1970-06-30 Monsanto Co Reinforcing fillers in a matrix of two thermosetting resins
US3567797A (en) * 1968-12-09 1971-03-02 Shell Oil Co Curable compositions comprising (a) a bis(1,2 - epoxyalkyl) cycloaliphatic compound,(b) a polyether polyepoxide and (c) a curing agent
US3812064A (en) * 1972-03-15 1974-05-21 Gen Electric Polyanhydrides useful as flexibilizing curing agents for epoxy resins
GB1358276A (en) * 1972-06-27 1974-07-03 British Railways Board Composites of carbon fibres and synthetic plastics materials
US3806489A (en) * 1973-06-04 1974-04-23 Rhone Progil Composite materials having an improved resilience
US4115599A (en) * 1974-11-06 1978-09-19 Owens-Illinois, Inc. Process for producing glass article having fragment retaining and alkali resistant coating
US3989673A (en) * 1974-12-30 1976-11-02 Hughes Aircraft Company Low temperature curing resin system
US4083735A (en) * 1977-03-29 1978-04-11 Caramanian John A Method of balancing rotors and composition therefor

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See references of WO8300159A1 *

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Publication number Publication date
WO1983000159A1 (en) 1983-01-20

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