CA2009546C - Thermally stabilized polyacrylonitrile polymers for carbon fiber manufacture - Google Patents
Thermally stabilized polyacrylonitrile polymers for carbon fiber manufactureInfo
- Publication number
- CA2009546C CA2009546C CA002009546A CA2009546A CA2009546C CA 2009546 C CA2009546 C CA 2009546C CA 002009546 A CA002009546 A CA 002009546A CA 2009546 A CA2009546 A CA 2009546A CA 2009546 C CA2009546 C CA 2009546C
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- precursor
- carbon fiber
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- atmosphere
- heated
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Classifications
-
- D—TEXTILES; PAPER
- D01—NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
- D01F—CHEMICAL FEATURES IN THE MANUFACTURE OF ARTIFICIAL FILAMENTS, THREADS, FIBRES, BRISTLES OR RIBBONS; APPARATUS SPECIALLY ADAPTED FOR THE MANUFACTURE OF CARBON FILAMENTS
- D01F9/00—Artificial filaments or the like of other substances; Manufacture thereof; Apparatus specially adapted for the manufacture of carbon filaments
- D01F9/08—Artificial filaments or the like of other substances; Manufacture thereof; Apparatus specially adapted for the manufacture of carbon filaments of inorganic material
- D01F9/12—Carbon filaments; Apparatus specially adapted for the manufacture thereof
- D01F9/14—Carbon filaments; Apparatus specially adapted for the manufacture thereof by decomposition of organic filaments
- D01F9/20—Carbon filaments; Apparatus specially adapted for the manufacture thereof by decomposition of organic filaments from polyaddition, polycondensation or polymerisation products
- D01F9/21—Carbon filaments; Apparatus specially adapted for the manufacture thereof by decomposition of organic filaments from polyaddition, polycondensation or polymerisation products from macromolecular compounds obtained by reactions only involving carbon-to-carbon unsaturated bonds
- D01F9/22—Carbon filaments; Apparatus specially adapted for the manufacture thereof by decomposition of organic filaments from polyaddition, polycondensation or polymerisation products from macromolecular compounds obtained by reactions only involving carbon-to-carbon unsaturated bonds from polyacrylonitriles
-
- D—TEXTILES; PAPER
- D01—NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
- D01F—CHEMICAL FEATURES IN THE MANUFACTURE OF ARTIFICIAL FILAMENTS, THREADS, FIBRES, BRISTLES OR RIBBONS; APPARATUS SPECIALLY ADAPTED FOR THE MANUFACTURE OF CARBON FILAMENTS
- D01F9/00—Artificial filaments or the like of other substances; Manufacture thereof; Apparatus specially adapted for the manufacture of carbon filaments
- D01F9/08—Artificial filaments or the like of other substances; Manufacture thereof; Apparatus specially adapted for the manufacture of carbon filaments of inorganic material
- D01F9/12—Carbon filaments; Apparatus specially adapted for the manufacture thereof
- D01F9/14—Carbon filaments; Apparatus specially adapted for the manufacture thereof by decomposition of organic filaments
- D01F9/20—Carbon filaments; Apparatus specially adapted for the manufacture thereof by decomposition of organic filaments from polyaddition, polycondensation or polymerisation products
- D01F9/21—Carbon filaments; Apparatus specially adapted for the manufacture thereof by decomposition of organic filaments from polyaddition, polycondensation or polymerisation products from macromolecular compounds obtained by reactions only involving carbon-to-carbon unsaturated bonds
- D01F9/22—Carbon filaments; Apparatus specially adapted for the manufacture thereof by decomposition of organic filaments from polyaddition, polycondensation or polymerisation products from macromolecular compounds obtained by reactions only involving carbon-to-carbon unsaturated bonds from polyacrylonitriles
- D01F9/225—Carbon filaments; Apparatus specially adapted for the manufacture thereof by decomposition of organic filaments from polyaddition, polycondensation or polymerisation products from macromolecular compounds obtained by reactions only involving carbon-to-carbon unsaturated bonds from polyacrylonitriles from stabilised polyacrylonitriles
Abstract
Disclosed is a process for manufacturing carbon fiber in which a polyacrylonitrile polymer in the form of a multitude of filaments is heated in an atmosphere that is substantially free of oxygen to form a thermally stabilized carbon fiber precursor in an oxygen-containing atmosphere to form a stabilized and oxidized precursor and then the thermally-stabilized precursor is heated in an oxygen-containing atmosphere to oxidize the precursor, which is then conventionally carbonized in an atmosphere substantially free of oxygen.
Description
20095~6 This invention relates to a process for manufacturing carbon fiber by carbonizing a precursor comprising a poly-acrylonitrile polymer, and more particularly to the stabilization of the precursor prior to carbonization.
Carbon fiber is useful in a variety of applications for which its mechanical, chemical and electrical properties are uniquely suited, particularly for making lightweight composites comprising the fiber in inorganic or organic matrices.
Although the cost of carbon fiber has been decreasing significantly even while its properties and reliability have been improved, there are still problems in some aspects of its production. In particular, the stabilization step in which polyacrylonitrile polymer, in the form of a tow comprising a multitude of filaments, is heated in air or other oxygen-containing gaseous medium prior to carbonization, adversely limits the rate at which carbon fiber can be manufactured on a commercial scale.
Such stabilization through oxidation is rate-limiting because of the risk of fusing the filaments or even causing an uncontrollable self-generating reaction (a "thermal run-away") if the precursor is heated too fast or too high during the stabilization. It is customary to use certain comonomers, such as acrylic acid, in forming the polyacrylonitrile polymer filaments in order to permit initiation of the oxidation reaction at a temperature lower than that otherwise required, e.g., between about 200 and 400C. There is a risk of thermal runaway even at such lower temperatures, but the risk is less and there is obviously less risk of fusion of the filaments.
However, to produce carbon fiber having uniform properties requires strict control of the amounts of the ,~ *
comonomer that is used to permit oxidation at lower temperatures, which presents production problems in addition to the rate limitation caused by the need to maintain a relatively low temperature.
The problems associated with the stabilization step have been extensively studied, for instance, in "Studies on Carbonization of Polyacrylonitrile Fibre - Part 5: Changes in Structure with Pyrolysis of Polyacrylonitrile Fibre" by Miyamichi, et al., Journal of Society of Fibre Science and Technology, Japan, 22, No. 12, 538 - 547 (1966).
U.S. Patent 4,104,004 suggests dividing up the stabilization step so that the precursor is heated in separate temperature zones, and U.S. Patents 3,775,520 and 3,954,950, while they suggest driving off residual solvent and producing controlled shrinkage by an initial brief heating step in an inert atmosphere prior to oxidizing the precursor, also limit the initial heating step to prevent stabilization from occurring.
There is still need for a process for manufacturing carbon fiber having uniform properties from a polyacrylonitrile polymer carbon fiber that reduces the risk of thermal runaway and fusion of the filaments while increasing the possible rates of reaction. It is also desirable to permit the use of polyacrylonitrile homopolymer, which is more economical to make than the comonomers conventionally used to reduce the temperature of oxidation.
According to the invention, a process for manufacturing carbon fiber in which a polyacrylonitrile polymer in the form of a multitude of filaments is heated in an oxygen-containing atmosphere to form a stabilized and oxidized precursor that is then carbonized in an atmosphere 'X`
20095~6 substantially free of oxygen, is characterized in that the polyacrylonitrile filaments are heated in an atmosphere that is substantially free of oxygen to form a thermally stabilized carbon fiber precursor prior to the step of heating the filaments in an oxygen-containing atmosphere to oxidize the thermally-stabilized precursor.
By that process, the precursor is readily and safely stabilized in a form that is capable of being oxidized for subsequent carbonization below the range of temperatures ordinarily used for oxidation, or alternatively permits the use of conventional oxidation temperatures or even higher temperatures to achieve a faster rate of oxidation. The carbonization conditions after oxidation follow the conventional procedures for making carbon fiber from polyacrylonitrile precursor.
Polyacrylonitrile polymers conventionally used as precursors for carbon fiber manufacture, and conventional procedures for the manufacture of such precursors are well known, for instance from U.S Patents 4,001,382, 4,009,248, 4,397,831 and 4,452,860. While the same polyacrylonitrile polymers are preferred as precursors for carbon fiber manufacture according to the invention, a greater variety of polyacrylonitrile polymers may be used. For example, polyacrylonitrile homopolymer may be used as a precursor and is readily stabilized by the process of this invention.
Preferably, the atmosphere that is substantially free of oxygen consists essentially of nitrogen or other inert gas, although a vacuum may be also used. The temperature to which the precursor is heated is preferably at least about 130C, more preferably at least about 230C but may be up to 500C or higher without risk of thermal runaway. Typically, one or more tows each comprising a multitude of continuous filaments travelling as a band are heated in a furnace or oven for stabilization in that inert atmosphere according to the invention. The stabilization step takes from a few minutes up to about an hour or more depending on the temperature chosen and may be conducted in a series of steps, if desired.
The duration of the stabilization step may be pre-determined by a conventional technique that measures thermal rearrangement, such as by differential scanning calorimetry (DSC). The reduction in residual heat of reaction measured by DSC in an inert atmosphere before and after the stabilization step is an appropriate measure of thermal rearrangement, and preferably is from about 10% to about 35%, more preferably by about 20%.
The diameter of filaments within the tow preferably ranges between 1 and 10 microns, although the magnitude of such diameter is not critical in accordance with this invention. Moreover, each tow may comprise between 500 and 20,000 filaments per tow. The conventional use of surface treatments on the filaments within the tow does not detract from the benefits of this invention.
After being thermally stabilized, the tows are may be oxidized at temperatures ranging surprisingly as low as room temperature or even lower, but it is preferred that oxidation take place in a gaseous medium containing oxygen such as air at temperatures ranging between 150C and 300C
for a time sufficient to allow these thermally stabilized tows to be self supporting (i.e., to retain dimensional integrity) during carbonization. Too high a temperature during oxidation is undesirable unless such heating takes place in apparatus for carrying away thermal decomposition products of the fiber being oxidized.
~ ~r 2009~46 While undergoing stabilization in the non-oxidizing atmosphere or oxidation, the band of filaments may be stretched to a length longer than its original length, held constant in length or allowed to shrink as desired.
After oxidation, the thermally stabilized and oxidized precursor tows are carbonized using conventional techniques for making carbon fibers. For example, the stabilized and oxidized precursor tow is heated in an inert atmosphere or vacuum at a temperature between about 500C and 800C for tar removal followed by heating at higher temperatures, also in nitrogen or other non-oxidizing atmosphere, to yield a carbonized fiber suitable for use with or without surface treatment according to conventional practice.
The following examples illustrate the invention, and Figures 1 - 14 graphically display the results of tests made according to the examples. The DSC apparatus used was a DuPont 910 DSC Module with a Model 1090 or like controller.
The X-axis in Figures 1 through llC is temperature in degrees centigrade. The Y-axis is heat flow in milliwatts.
Figures 12, 13 and 14 show load (tension) in grams per denier versus degree of reaction in percent. The degree of reaction is determined using density.
The sample size in Figure 1 was 1.136 milligrams. The rate of temperature increase was 10 degrees centigrade per minute and was in air. The sample size in Figure 2 was 1.110 milligrams and the rate of temperature increase was 10 degrees centigrade per minute in nitrogen. The sample type and rate of temperature increase are set forth below for the data in Figures 3 - llC.
X
`- 2009S46 8ample Figure 8ize Type Rate 3 1.332 mg AB 10 4 1.396 mg CE 10 1.369 mg AB 10 6 1.320 mg CE 10 7 0.243 mg AB 10 8 0.791 mg CE 10 9 1.246 mg DUP 10 8.826 mg DUP 10 11 4.624 mg DUP 10 llA 1.332 mg DUP 10 llB 1.327 mg DUP lO
llC 3.178 mg DUP 10 In Figures 1 and 2 DSC was respectively in air and nitrogen. DSC of Figures 3 and 4 was in nitrogen. DSC was in air for Figures 5, 6 (both purge) and 7 and 8 (second heating). Figuré 9 of the DSC was in air (purge) and DSC
was in nitrogen (Figure 10) and then in air in Figure 11.
Figure llA was run in nitrogen; Figure llB run in air; and Figure llC is rerun in air after initial heating in nitrogen.
Examples In the work described below "AB Precursor" and "CE
Precursor" are standard carbon fiber precursors made from acrylonitrile and methacrylic acid (2 weight ~) in the case of the AB precursor and acrylonitrile, methylacrylate and itaconic acid in case of the CE precursor.
Several experiments were initially run with varying degrees of nitrogen (N2) pretreatment and then analyzed thermally. As seen in Figures 1 and 2, the amount of change ~`
in heats of decomposition (HD) between precursor heated in air and heated in nitrogen (N2) were different. These differences are typical for acrylic polymers heated in oxygen containing and oxygen free atmospheres with the low HD (in N2) due to thermal rearrangement reactions and the large HD in air due to thermal rearrangement and oxidation reactions. Table 1 shows the results of two experiments where precursor was first pretreated in N2 at elevated temperatures.
HEATæ OF DECOMPOæITION IN AIR AND N2 HD
Air Cal/gm -2 AB Precursor (Baseline) 1121 165 Pretreatment:
235D, 55 min in N2 943 116 Pretreatment:
235C, 116 min in N2 844 90.8 The change in HD was 178 cal/g when heated in air after pretreatment in N2 but only 49 cal/g when heated in N2 after the same nitrogen pretreatment for the first sample and 277 cal/g when heated in air after pretreatment and only 74 cal/g when heated in N2 after pretreatment for the second.
Since the pretreatment heating was carried out in N2, it might be expected that the change in HD would be the same in both air and N2. However, from this data at least part of the oxidation reaction is not involved with or linked to the rearrangement reaction. If the sample 1 pretreatment (235OC/55 min) had been run in air instead of N2, the residual HD' air would be 740 cal/g. The N2 preheat generated only 49 cal/g, but lowered the HD' air by 178 '~ ~
200g~4~
cal/g, so it appears that 129 cal/g of reaction with oxygen was by-passed by the N2 preheat. The N2 preheat for 116 min at 235C generated 74 cal/g and lowered the HDI air by 277 cal/g so it by-passed 203 cal/g of the expected reaction with oxygen. It is evident that the chemical structure of the fiber is different when preheated in N2 prior to air oxidation.
Samples of four different polyacrylonitrile polymers were thermally analyzed in nitrogen and air to better define the mechanisms that were occurring. As part of the analysis, ground precursor fiber was first analyzed in nitrogen, up to about 430C. The results are shown in Figure 3 (AB Precursor) and 4 (CE Precursor). The results were not unusual; an exponentially-increasing heat evolution peaking at about 285-290C, followed by a rapid heat decrease to give about 100-135 cal/g evolved heat. The resultant thermally-stabilized powder was then reweighed and reanalysed, this time in air. Normally the air oxidation curve will follow the route shown in Figure-5 (AB Precursor) and Figure 6 (CE Precursor). Instead, the curve shape was markedly changed. The area under the curve was significantly reduced, from about 1000-1100 caljg to about 250 cal/g for AB Precursor and 335 cal/g for CE Precursor.
In addition, the oxidation-initiation temperature was reduced about 20C, indicating that the oxidation would be more rapid than non-prestabilized fiber (Figures 7 and 8).
Additionally, the position of the two major thermal peaks shifted. For the AB Precursor the shift was more dramatic, with the lower peak dropping from a typical 228C to 212C.
The position of the higher-temperature peak increased from 326C to 360C for AB Precursor while it decreased for CE
Precursor from 330C to 315C.
,,3- ~,~
9 2009~46 These results suggest a major change in the oxidation reactions. There appear to be more oxidatively-active sites after the nitrogen pretreatment as evidenced by the decrease in initiation temperature. There also appears to be less overall oxidation, or possibly less dehydrogenation, as evidenced by the higher temperature which may imply more oxidative stability or may simply mean that the influence of the lower-temperature reactions is dissipated leaving only the higher-temperature part of the response.
The thermal analysis of DuPont T-42 polymer, a commercial grade polyacrylonitrile polymer fiber, in air (Figure 9) indicates that it would be a less suitable precursor than AB Precursor due to its high initiation temperature and rapid heat evolution rate. If the precursor is first prestabilized in N2 (Figure 10) and then reheated in air (Figure 11), the thermal response changes dramatically, similar to what has been seen with the other acrylic polymers. The reaction initiation temperature has decreased substantially, the single peak has split into two very distinct peaks, and the total heat of reaction is only 34 cal/gm.
PAN homopolymer, which is typically avoided at present as a carbon fiber precursor in commercial practice because of its slow reaction rate, high rate of that evolution once it begins to react, and high initiation temperature was also found to undergo dramatic changes in thermal characteristics once it was prestabilized. Figure llA shows the typical DSC
curve for this polymer in nitrogen with a heat of decomposition of 124 cal/gm, while Figure llB shows the thermal curve in air. The heat of reaction in air (1103 cal/gm) is typical of other acrylic polymers, but the homopolymer is characterized by a high initiation - 10 - 20095~6 temperature (250C) and rapid heat evolution rate (steep slope). When the polymer is prestabilized by running the DSC in nitrogen and then rerun in air, the changes are dramatic (Figure llC). The initiation temperature drops to 155C with the single peak splitting into two distinct peaks, the rate of heat evolution drops significantly as evidenced by a change in initial slope (note change in y-axis range between Figures llB and llC), and the overall heat of reaction has dropped to 237 cal/gm. Those results indicate the polymer may make a much more suitable carbon fiber precursor from the standpoint of ease of processability, safety, and potentially, economics.
These data also suggest that the fiber will be more easily oxidized after prestabilization. As such, a fiber that has been prestabilized and oxidized for a given time at temperature will have a higher density than a fiber that is only oxidized for the same time at temperature. A set of experiments was run to determine if this is true; the results are shown in Table 2 below.
Density Conditions ~g/cc) 235C, 2 hr, air 1.2688 235C, 1 hr, N2; then 235C, 1 hr, air 1.2904 235C, 1 hr, air 235C, 1 hr, N2 1.2101 X
003S~6 The fiber that has been prestabilized and oxidized does exhibit a higher density than the fiber that has just been oxidized at the same temperature for the same amount of time. This is believed due to the increase in reactivity after prestabilization since prestabilization alone results in a rate of density increase that is less than that due to oxidation in air (Table 2 and Figure 12). Looking at the density difference between the oxidized and prestabilized/oxidized fibers and assuming kinetics similar to the reaction kinetics of the AB Precursor for comparison purposes, the increase in oxidized fiber density due to prestabilization corresponds to a time savings of 40 minutes at 235C. That is, in order to reach the same oxidized density as the prestabilized/oxidized fiber, the precursor fiber would have to be oxidized for 160 minutes at 235C
instead of stabilized/oxidized for a total of 120 minutes at 235C.
Another way to monitor the reaction characteristics of an acrylic based precursor is to follow the tension that is generated as the fiber rearranges and oxidizes at elevated temperatures. Tension vs time data were generated for AB
and DuPont precursors and prestabilized fibers to further clarify changes in oxidation reaction characteristics that are caused by prestabilization in an inert atmosphere.
Figure 13 shows load/time data for AB precursor in air at 235C, N2 at 235C, and for AB prestabilized for varying amounts of time and then run in air at 235C. Comparing the samples run in air and N2 (no stabilization), both samples show the characteristic drop in tension initially followed by a tension increase as the fiber beings to react. The tension increase due to the shrinkage of the sample run in N2 is significantly less than in air, the difference xi -20095~6 presumably being due to the added shrinkage of the oxidation reactlons occurrlng ln alr.
The prestabilized fibers show a sudden increase in tension when run in air possibly indicating an initial increase in the degree of reactivity. The load build up quickly levels out for the 60 minute prestabilized fiber, followed by 30 minute, and 5 minute which has a final load after 60 minutes, similar to AB Precursor. These lower oxidation loads could be due to a lower overall oxidation reactivity for the prestabilized fibers that would agree with DTA results showing lower than expected residual heats of reaction in air after prestabilization.
The results for the DuPont T-42 type fiber are shown in Figure 14. This fiber is characteristically slower to react than AB as evidenced by the slow load buildup for the AB 10 Precursor. After prestabilization, the shrinkage character-istics of the fiber are greatly altered. The tension increase with time, while not as great as for AB Precursor, is similar in shape, indicating the fiber may oxidize more readily after prestabilization. As with the prestabilized AB Precursor samples, the T-42 type fibers show a rapid initial increase in tension (the greater the degree of prestabilization, the greater the rate of tension buildup).
After 60 minutes, the more highly prestabilized fiber has a lower load buildup than the other prestabilized fiber (similar to AB results) but both samples are significantly higher than the baseline indicating the prestabilization (even after as little as five minutes) results in an increase in oxidation reaction rate, but may reduce the number of sites available for reaction. These results indicate that prestabilization can be used to make certain X;
200~9~i~6 precursor fibers more reactive while also increasing the safety of the process by reducing the oxidation exotherm.
Another interesting finding from these experiments is that prestabilization changes fiber reactively sufficiently to cause a subsequent reaction in air at room temperature.
A set of AB fibers were stabilized in N2 at 250C for times ranging from 5 minutes to 6 hours. In each case, the sample was then divided in half, with half placed in an inert atmosphere and the other half stored in air, both at room temperature. In all cases, the sample in air continued to change colour and slowly darken while the sample in N2 remains golden brown. It was found that this reaction could be suspended by placing the partially darkened sample in N2 and then reinitiated by exposing again to air. The fibers exposed to air after prestabilization were able to oxidize at room temperature. If oxidation type reactions were indeed occurring, it would be expected that the residual heat of reaction would decrease with increasing time of exposure to air at room temperature. A series of experiments was performed to determine if this was indeed the case. In one set of experiments, a length of AB
Precursor was stabilized in N2 for 2 hours at 250C; the fiber was divided in half with half exposed to room-temperature air for 3 hours and the other half exposed to air for 24 hours. The samples were then restored in N2 and submitted for thermal analysis. In all cases, the thermal lab was careful to run the samples as quickly as possible after the N2 seal was broken. In the second experiment, a sample of AB precursor was stabilized for 16 hours at 250C
in N2 and then divided with parts exposed for 0 hours, 1 hour, 3 hours, and 24 hours in air. Samples were then _, restored in N2 and thermally analyzed. The results are shown in Table 3 below:
CHANGE IN Hair OF 8TABILIZBD FIBERB AFTER
8tabilization Conditions Air Exposure Time in N2 at Room Temperature ~hr) Hair 2 hours at 250C 3 684 2 hours at 250C 24 624 16 hours at 250C 0 678 16 hours at 250C 1 652 16 hours at 250C 3 605 16 hours at 250C 24 548 For both sets of these experiments, the heat of reaction decreased with time of exposure in air, indicating a reaction occurring at room temperature which is responsible for the colour change we had noted. A
stabilized fiber was also run to determine if free radicals are present, which might be initiating the reaction at room temperature in air. The results indicated the presence of some free radical activity, which is as yet unidentified.
.
X
Carbon fiber is useful in a variety of applications for which its mechanical, chemical and electrical properties are uniquely suited, particularly for making lightweight composites comprising the fiber in inorganic or organic matrices.
Although the cost of carbon fiber has been decreasing significantly even while its properties and reliability have been improved, there are still problems in some aspects of its production. In particular, the stabilization step in which polyacrylonitrile polymer, in the form of a tow comprising a multitude of filaments, is heated in air or other oxygen-containing gaseous medium prior to carbonization, adversely limits the rate at which carbon fiber can be manufactured on a commercial scale.
Such stabilization through oxidation is rate-limiting because of the risk of fusing the filaments or even causing an uncontrollable self-generating reaction (a "thermal run-away") if the precursor is heated too fast or too high during the stabilization. It is customary to use certain comonomers, such as acrylic acid, in forming the polyacrylonitrile polymer filaments in order to permit initiation of the oxidation reaction at a temperature lower than that otherwise required, e.g., between about 200 and 400C. There is a risk of thermal runaway even at such lower temperatures, but the risk is less and there is obviously less risk of fusion of the filaments.
However, to produce carbon fiber having uniform properties requires strict control of the amounts of the ,~ *
comonomer that is used to permit oxidation at lower temperatures, which presents production problems in addition to the rate limitation caused by the need to maintain a relatively low temperature.
The problems associated with the stabilization step have been extensively studied, for instance, in "Studies on Carbonization of Polyacrylonitrile Fibre - Part 5: Changes in Structure with Pyrolysis of Polyacrylonitrile Fibre" by Miyamichi, et al., Journal of Society of Fibre Science and Technology, Japan, 22, No. 12, 538 - 547 (1966).
U.S. Patent 4,104,004 suggests dividing up the stabilization step so that the precursor is heated in separate temperature zones, and U.S. Patents 3,775,520 and 3,954,950, while they suggest driving off residual solvent and producing controlled shrinkage by an initial brief heating step in an inert atmosphere prior to oxidizing the precursor, also limit the initial heating step to prevent stabilization from occurring.
There is still need for a process for manufacturing carbon fiber having uniform properties from a polyacrylonitrile polymer carbon fiber that reduces the risk of thermal runaway and fusion of the filaments while increasing the possible rates of reaction. It is also desirable to permit the use of polyacrylonitrile homopolymer, which is more economical to make than the comonomers conventionally used to reduce the temperature of oxidation.
According to the invention, a process for manufacturing carbon fiber in which a polyacrylonitrile polymer in the form of a multitude of filaments is heated in an oxygen-containing atmosphere to form a stabilized and oxidized precursor that is then carbonized in an atmosphere 'X`
20095~6 substantially free of oxygen, is characterized in that the polyacrylonitrile filaments are heated in an atmosphere that is substantially free of oxygen to form a thermally stabilized carbon fiber precursor prior to the step of heating the filaments in an oxygen-containing atmosphere to oxidize the thermally-stabilized precursor.
By that process, the precursor is readily and safely stabilized in a form that is capable of being oxidized for subsequent carbonization below the range of temperatures ordinarily used for oxidation, or alternatively permits the use of conventional oxidation temperatures or even higher temperatures to achieve a faster rate of oxidation. The carbonization conditions after oxidation follow the conventional procedures for making carbon fiber from polyacrylonitrile precursor.
Polyacrylonitrile polymers conventionally used as precursors for carbon fiber manufacture, and conventional procedures for the manufacture of such precursors are well known, for instance from U.S Patents 4,001,382, 4,009,248, 4,397,831 and 4,452,860. While the same polyacrylonitrile polymers are preferred as precursors for carbon fiber manufacture according to the invention, a greater variety of polyacrylonitrile polymers may be used. For example, polyacrylonitrile homopolymer may be used as a precursor and is readily stabilized by the process of this invention.
Preferably, the atmosphere that is substantially free of oxygen consists essentially of nitrogen or other inert gas, although a vacuum may be also used. The temperature to which the precursor is heated is preferably at least about 130C, more preferably at least about 230C but may be up to 500C or higher without risk of thermal runaway. Typically, one or more tows each comprising a multitude of continuous filaments travelling as a band are heated in a furnace or oven for stabilization in that inert atmosphere according to the invention. The stabilization step takes from a few minutes up to about an hour or more depending on the temperature chosen and may be conducted in a series of steps, if desired.
The duration of the stabilization step may be pre-determined by a conventional technique that measures thermal rearrangement, such as by differential scanning calorimetry (DSC). The reduction in residual heat of reaction measured by DSC in an inert atmosphere before and after the stabilization step is an appropriate measure of thermal rearrangement, and preferably is from about 10% to about 35%, more preferably by about 20%.
The diameter of filaments within the tow preferably ranges between 1 and 10 microns, although the magnitude of such diameter is not critical in accordance with this invention. Moreover, each tow may comprise between 500 and 20,000 filaments per tow. The conventional use of surface treatments on the filaments within the tow does not detract from the benefits of this invention.
After being thermally stabilized, the tows are may be oxidized at temperatures ranging surprisingly as low as room temperature or even lower, but it is preferred that oxidation take place in a gaseous medium containing oxygen such as air at temperatures ranging between 150C and 300C
for a time sufficient to allow these thermally stabilized tows to be self supporting (i.e., to retain dimensional integrity) during carbonization. Too high a temperature during oxidation is undesirable unless such heating takes place in apparatus for carrying away thermal decomposition products of the fiber being oxidized.
~ ~r 2009~46 While undergoing stabilization in the non-oxidizing atmosphere or oxidation, the band of filaments may be stretched to a length longer than its original length, held constant in length or allowed to shrink as desired.
After oxidation, the thermally stabilized and oxidized precursor tows are carbonized using conventional techniques for making carbon fibers. For example, the stabilized and oxidized precursor tow is heated in an inert atmosphere or vacuum at a temperature between about 500C and 800C for tar removal followed by heating at higher temperatures, also in nitrogen or other non-oxidizing atmosphere, to yield a carbonized fiber suitable for use with or without surface treatment according to conventional practice.
The following examples illustrate the invention, and Figures 1 - 14 graphically display the results of tests made according to the examples. The DSC apparatus used was a DuPont 910 DSC Module with a Model 1090 or like controller.
The X-axis in Figures 1 through llC is temperature in degrees centigrade. The Y-axis is heat flow in milliwatts.
Figures 12, 13 and 14 show load (tension) in grams per denier versus degree of reaction in percent. The degree of reaction is determined using density.
The sample size in Figure 1 was 1.136 milligrams. The rate of temperature increase was 10 degrees centigrade per minute and was in air. The sample size in Figure 2 was 1.110 milligrams and the rate of temperature increase was 10 degrees centigrade per minute in nitrogen. The sample type and rate of temperature increase are set forth below for the data in Figures 3 - llC.
X
`- 2009S46 8ample Figure 8ize Type Rate 3 1.332 mg AB 10 4 1.396 mg CE 10 1.369 mg AB 10 6 1.320 mg CE 10 7 0.243 mg AB 10 8 0.791 mg CE 10 9 1.246 mg DUP 10 8.826 mg DUP 10 11 4.624 mg DUP 10 llA 1.332 mg DUP 10 llB 1.327 mg DUP lO
llC 3.178 mg DUP 10 In Figures 1 and 2 DSC was respectively in air and nitrogen. DSC of Figures 3 and 4 was in nitrogen. DSC was in air for Figures 5, 6 (both purge) and 7 and 8 (second heating). Figuré 9 of the DSC was in air (purge) and DSC
was in nitrogen (Figure 10) and then in air in Figure 11.
Figure llA was run in nitrogen; Figure llB run in air; and Figure llC is rerun in air after initial heating in nitrogen.
Examples In the work described below "AB Precursor" and "CE
Precursor" are standard carbon fiber precursors made from acrylonitrile and methacrylic acid (2 weight ~) in the case of the AB precursor and acrylonitrile, methylacrylate and itaconic acid in case of the CE precursor.
Several experiments were initially run with varying degrees of nitrogen (N2) pretreatment and then analyzed thermally. As seen in Figures 1 and 2, the amount of change ~`
in heats of decomposition (HD) between precursor heated in air and heated in nitrogen (N2) were different. These differences are typical for acrylic polymers heated in oxygen containing and oxygen free atmospheres with the low HD (in N2) due to thermal rearrangement reactions and the large HD in air due to thermal rearrangement and oxidation reactions. Table 1 shows the results of two experiments where precursor was first pretreated in N2 at elevated temperatures.
HEATæ OF DECOMPOæITION IN AIR AND N2 HD
Air Cal/gm -2 AB Precursor (Baseline) 1121 165 Pretreatment:
235D, 55 min in N2 943 116 Pretreatment:
235C, 116 min in N2 844 90.8 The change in HD was 178 cal/g when heated in air after pretreatment in N2 but only 49 cal/g when heated in N2 after the same nitrogen pretreatment for the first sample and 277 cal/g when heated in air after pretreatment and only 74 cal/g when heated in N2 after pretreatment for the second.
Since the pretreatment heating was carried out in N2, it might be expected that the change in HD would be the same in both air and N2. However, from this data at least part of the oxidation reaction is not involved with or linked to the rearrangement reaction. If the sample 1 pretreatment (235OC/55 min) had been run in air instead of N2, the residual HD' air would be 740 cal/g. The N2 preheat generated only 49 cal/g, but lowered the HD' air by 178 '~ ~
200g~4~
cal/g, so it appears that 129 cal/g of reaction with oxygen was by-passed by the N2 preheat. The N2 preheat for 116 min at 235C generated 74 cal/g and lowered the HDI air by 277 cal/g so it by-passed 203 cal/g of the expected reaction with oxygen. It is evident that the chemical structure of the fiber is different when preheated in N2 prior to air oxidation.
Samples of four different polyacrylonitrile polymers were thermally analyzed in nitrogen and air to better define the mechanisms that were occurring. As part of the analysis, ground precursor fiber was first analyzed in nitrogen, up to about 430C. The results are shown in Figure 3 (AB Precursor) and 4 (CE Precursor). The results were not unusual; an exponentially-increasing heat evolution peaking at about 285-290C, followed by a rapid heat decrease to give about 100-135 cal/g evolved heat. The resultant thermally-stabilized powder was then reweighed and reanalysed, this time in air. Normally the air oxidation curve will follow the route shown in Figure-5 (AB Precursor) and Figure 6 (CE Precursor). Instead, the curve shape was markedly changed. The area under the curve was significantly reduced, from about 1000-1100 caljg to about 250 cal/g for AB Precursor and 335 cal/g for CE Precursor.
In addition, the oxidation-initiation temperature was reduced about 20C, indicating that the oxidation would be more rapid than non-prestabilized fiber (Figures 7 and 8).
Additionally, the position of the two major thermal peaks shifted. For the AB Precursor the shift was more dramatic, with the lower peak dropping from a typical 228C to 212C.
The position of the higher-temperature peak increased from 326C to 360C for AB Precursor while it decreased for CE
Precursor from 330C to 315C.
,,3- ~,~
9 2009~46 These results suggest a major change in the oxidation reactions. There appear to be more oxidatively-active sites after the nitrogen pretreatment as evidenced by the decrease in initiation temperature. There also appears to be less overall oxidation, or possibly less dehydrogenation, as evidenced by the higher temperature which may imply more oxidative stability or may simply mean that the influence of the lower-temperature reactions is dissipated leaving only the higher-temperature part of the response.
The thermal analysis of DuPont T-42 polymer, a commercial grade polyacrylonitrile polymer fiber, in air (Figure 9) indicates that it would be a less suitable precursor than AB Precursor due to its high initiation temperature and rapid heat evolution rate. If the precursor is first prestabilized in N2 (Figure 10) and then reheated in air (Figure 11), the thermal response changes dramatically, similar to what has been seen with the other acrylic polymers. The reaction initiation temperature has decreased substantially, the single peak has split into two very distinct peaks, and the total heat of reaction is only 34 cal/gm.
PAN homopolymer, which is typically avoided at present as a carbon fiber precursor in commercial practice because of its slow reaction rate, high rate of that evolution once it begins to react, and high initiation temperature was also found to undergo dramatic changes in thermal characteristics once it was prestabilized. Figure llA shows the typical DSC
curve for this polymer in nitrogen with a heat of decomposition of 124 cal/gm, while Figure llB shows the thermal curve in air. The heat of reaction in air (1103 cal/gm) is typical of other acrylic polymers, but the homopolymer is characterized by a high initiation - 10 - 20095~6 temperature (250C) and rapid heat evolution rate (steep slope). When the polymer is prestabilized by running the DSC in nitrogen and then rerun in air, the changes are dramatic (Figure llC). The initiation temperature drops to 155C with the single peak splitting into two distinct peaks, the rate of heat evolution drops significantly as evidenced by a change in initial slope (note change in y-axis range between Figures llB and llC), and the overall heat of reaction has dropped to 237 cal/gm. Those results indicate the polymer may make a much more suitable carbon fiber precursor from the standpoint of ease of processability, safety, and potentially, economics.
These data also suggest that the fiber will be more easily oxidized after prestabilization. As such, a fiber that has been prestabilized and oxidized for a given time at temperature will have a higher density than a fiber that is only oxidized for the same time at temperature. A set of experiments was run to determine if this is true; the results are shown in Table 2 below.
Density Conditions ~g/cc) 235C, 2 hr, air 1.2688 235C, 1 hr, N2; then 235C, 1 hr, air 1.2904 235C, 1 hr, air 235C, 1 hr, N2 1.2101 X
003S~6 The fiber that has been prestabilized and oxidized does exhibit a higher density than the fiber that has just been oxidized at the same temperature for the same amount of time. This is believed due to the increase in reactivity after prestabilization since prestabilization alone results in a rate of density increase that is less than that due to oxidation in air (Table 2 and Figure 12). Looking at the density difference between the oxidized and prestabilized/oxidized fibers and assuming kinetics similar to the reaction kinetics of the AB Precursor for comparison purposes, the increase in oxidized fiber density due to prestabilization corresponds to a time savings of 40 minutes at 235C. That is, in order to reach the same oxidized density as the prestabilized/oxidized fiber, the precursor fiber would have to be oxidized for 160 minutes at 235C
instead of stabilized/oxidized for a total of 120 minutes at 235C.
Another way to monitor the reaction characteristics of an acrylic based precursor is to follow the tension that is generated as the fiber rearranges and oxidizes at elevated temperatures. Tension vs time data were generated for AB
and DuPont precursors and prestabilized fibers to further clarify changes in oxidation reaction characteristics that are caused by prestabilization in an inert atmosphere.
Figure 13 shows load/time data for AB precursor in air at 235C, N2 at 235C, and for AB prestabilized for varying amounts of time and then run in air at 235C. Comparing the samples run in air and N2 (no stabilization), both samples show the characteristic drop in tension initially followed by a tension increase as the fiber beings to react. The tension increase due to the shrinkage of the sample run in N2 is significantly less than in air, the difference xi -20095~6 presumably being due to the added shrinkage of the oxidation reactlons occurrlng ln alr.
The prestabilized fibers show a sudden increase in tension when run in air possibly indicating an initial increase in the degree of reactivity. The load build up quickly levels out for the 60 minute prestabilized fiber, followed by 30 minute, and 5 minute which has a final load after 60 minutes, similar to AB Precursor. These lower oxidation loads could be due to a lower overall oxidation reactivity for the prestabilized fibers that would agree with DTA results showing lower than expected residual heats of reaction in air after prestabilization.
The results for the DuPont T-42 type fiber are shown in Figure 14. This fiber is characteristically slower to react than AB as evidenced by the slow load buildup for the AB 10 Precursor. After prestabilization, the shrinkage character-istics of the fiber are greatly altered. The tension increase with time, while not as great as for AB Precursor, is similar in shape, indicating the fiber may oxidize more readily after prestabilization. As with the prestabilized AB Precursor samples, the T-42 type fibers show a rapid initial increase in tension (the greater the degree of prestabilization, the greater the rate of tension buildup).
After 60 minutes, the more highly prestabilized fiber has a lower load buildup than the other prestabilized fiber (similar to AB results) but both samples are significantly higher than the baseline indicating the prestabilization (even after as little as five minutes) results in an increase in oxidation reaction rate, but may reduce the number of sites available for reaction. These results indicate that prestabilization can be used to make certain X;
200~9~i~6 precursor fibers more reactive while also increasing the safety of the process by reducing the oxidation exotherm.
Another interesting finding from these experiments is that prestabilization changes fiber reactively sufficiently to cause a subsequent reaction in air at room temperature.
A set of AB fibers were stabilized in N2 at 250C for times ranging from 5 minutes to 6 hours. In each case, the sample was then divided in half, with half placed in an inert atmosphere and the other half stored in air, both at room temperature. In all cases, the sample in air continued to change colour and slowly darken while the sample in N2 remains golden brown. It was found that this reaction could be suspended by placing the partially darkened sample in N2 and then reinitiated by exposing again to air. The fibers exposed to air after prestabilization were able to oxidize at room temperature. If oxidation type reactions were indeed occurring, it would be expected that the residual heat of reaction would decrease with increasing time of exposure to air at room temperature. A series of experiments was performed to determine if this was indeed the case. In one set of experiments, a length of AB
Precursor was stabilized in N2 for 2 hours at 250C; the fiber was divided in half with half exposed to room-temperature air for 3 hours and the other half exposed to air for 24 hours. The samples were then restored in N2 and submitted for thermal analysis. In all cases, the thermal lab was careful to run the samples as quickly as possible after the N2 seal was broken. In the second experiment, a sample of AB precursor was stabilized for 16 hours at 250C
in N2 and then divided with parts exposed for 0 hours, 1 hour, 3 hours, and 24 hours in air. Samples were then _, restored in N2 and thermally analyzed. The results are shown in Table 3 below:
CHANGE IN Hair OF 8TABILIZBD FIBERB AFTER
8tabilization Conditions Air Exposure Time in N2 at Room Temperature ~hr) Hair 2 hours at 250C 3 684 2 hours at 250C 24 624 16 hours at 250C 0 678 16 hours at 250C 1 652 16 hours at 250C 3 605 16 hours at 250C 24 548 For both sets of these experiments, the heat of reaction decreased with time of exposure in air, indicating a reaction occurring at room temperature which is responsible for the colour change we had noted. A
stabilized fiber was also run to determine if free radicals are present, which might be initiating the reaction at room temperature in air. The results indicated the presence of some free radical activity, which is as yet unidentified.
.
X
Claims (7)
1. A process for manufacturing carbon fiber in which a polyacrylontrile polymer in the form of a multitude of filaments is heated in an oxygen-containing atmosphere to form a stabilized and oxidized precursor that is then carbonized in an atmosphere substantially free of oxygen, is characterized in that the polyacrylonitrile filaments are heated in an atmosphere that is substantially free of oxygen to form a thermally stabilized carbon fiber precursor prior to the step of heating the filaments in an oxygen-containing atmosphere to oxidize the thermally-stabilized precursor.
2. A process for manufacturing carbon fiber as claimed in claim 1, further characterized in that the temperature to which the polyacrylonitrile filaments are heated in an atmosphere that is substantially free of oxygen is heated is preferably at least about 230°.
3. A process for manufacturing carbon fiber as claimed in claim 1, further characterized in that the atmosphere that is substantially free of oxygen is nitrogen.
4. A process for manufacturing carbon fiber as claimed in claim 1, 2 or 3, further characterized in that the poly-acrylonitrile filaments are heated in an atmosphere that is substantially free of oxygen until the reduction in residual heat of reaction as measured by differential scanning calorimetry is from about 10% to about 35%.
5. A process for manufacturing carbon fiber as claimed in claim 4, further characterized in that the filaments are heated until the reduction in residual heat of reaction is about 20%.
6. A process for manufacturing carbon fiber as claimed in any of the preceding claims, further characterized in that the thermally stabilized carbon fiber precursor in the form of a tow is heated in an oxygen-containing atmosphere at a temperature from 150°C to 300°C for a time sufficient to allow the tow to be self-supporting.
7. A process for manufacturing carbon fiber as claimed in any of the preceding claims, further characterized in that the polyacrylonitrile filaments in the form of a band of closely spaced tows are moved in an atmosphere that is substantially free of oxygen through an oven maintained at a first range of temperatures to heat the filaments to form a thermally stabilized carbon fiber precursor and then are moved at a higher line speed in an oxygen-containing atmosphere through an oven maintained at a second range of temperatures to oxidize the thermally-stabilized precursor.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US31453889A | 1989-02-23 | 1989-02-23 | |
| US314,538 | 1989-02-23 |
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| Publication Number | Publication Date |
|---|---|
| CA2009546A1 CA2009546A1 (en) | 1990-08-23 |
| CA2009546C true CA2009546C (en) | 1996-05-28 |
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ID=23220353
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA002009546A Expired - Fee Related CA2009546C (en) | 1989-02-23 | 1990-02-07 | Thermally stabilized polyacrylonitrile polymers for carbon fiber manufacture |
Country Status (7)
| Country | Link |
|---|---|
| EP (1) | EP0384299B1 (en) |
| JP (1) | JPH038812A (en) |
| KR (1) | KR0147849B1 (en) |
| CA (1) | CA2009546C (en) |
| DE (1) | DE69031690T2 (en) |
| ES (1) | ES2109224T3 (en) |
| IL (1) | IL93475A (en) |
Families Citing this family (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5256344A (en) * | 1989-02-23 | 1993-10-26 | Hercules Incorporated | Process of thermally stabilizing pan fibers |
| DE19517911A1 (en) * | 1995-05-16 | 1996-11-21 | Sgl Technik Gmbh | Process for converting multi-dimensional sheet-like structures consisting of polyacrylonitrile fibers into the thermally stabilized state |
| EP2147776A1 (en) | 2008-07-23 | 2010-01-27 | SGL Carbon SE | Method for manufacturing a compound material reinforced with fibre netting and compound material reinforced with fibre netting and its application |
| DE102009047491A1 (en) | 2009-12-04 | 2011-06-09 | Sgl Carbon Se | Production of a 3D textile structure and semifinished fiber products from fiber composites |
| CN101922065B (en) * | 2010-09-16 | 2011-12-07 | 中国科学院西安光学精密机械研究所 | Method for pre-oxidizing polyacrylonitrile-based carbon fiber precursors |
| KR102530253B1 (en) * | 2017-10-10 | 2023-05-09 | 디킨 유니버시티 | Precursor Stabilisation Process |
| JP7268285B2 (en) * | 2017-10-10 | 2023-05-08 | ディーキン ユニバーシティ | Reactor, Apparatus and System for Prestabilizing Polyacrylonitrile (PAN) Precursors Used in Carbon Fiber Production |
| CN112708967B (en) * | 2019-10-24 | 2022-10-11 | 中国石油化工股份有限公司 | Pre-oxidation method of polyacrylonitrile-based fiber and preparation method of carbon fiber |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| GB1245123A (en) * | 1968-06-04 | 1971-09-08 | Rolls Royce | A method of manufacturing carbon fibres |
| US3961888A (en) * | 1968-09-18 | 1976-06-08 | Celanese Corporation | Acrylic fiber conversion utilizing a stabilization treatment conducted initially in an essentially inert atmosphere |
| US3775520A (en) * | 1970-03-09 | 1973-11-27 | Celanese Corp | Carbonization/graphitization of poly-acrylonitrile fibers containing residual spinning solvent |
-
1990
- 1990-02-07 CA CA002009546A patent/CA2009546C/en not_active Expired - Fee Related
- 1990-02-15 DE DE69031690T patent/DE69031690T2/en not_active Expired - Fee Related
- 1990-02-15 ES ES90102972T patent/ES2109224T3/en not_active Expired - Lifetime
- 1990-02-15 EP EP90102972A patent/EP0384299B1/en not_active Expired - Lifetime
- 1990-02-21 IL IL93475A patent/IL93475A/en not_active IP Right Cessation
- 1990-02-22 KR KR1019900002219A patent/KR0147849B1/en not_active IP Right Cessation
- 1990-02-23 JP JP2044245A patent/JPH038812A/en active Pending
Also Published As
| Publication number | Publication date |
|---|---|
| EP0384299A3 (en) | 1991-11-06 |
| JPH038812A (en) | 1991-01-16 |
| KR900013120A (en) | 1990-09-03 |
| IL93475A (en) | 1992-08-18 |
| KR0147849B1 (en) | 1998-08-01 |
| EP0384299A2 (en) | 1990-08-29 |
| IL93475A0 (en) | 1990-11-29 |
| DE69031690D1 (en) | 1997-12-18 |
| ES2109224T3 (en) | 1998-01-16 |
| EP0384299B1 (en) | 1997-11-12 |
| DE69031690T2 (en) | 1998-03-12 |
| CA2009546A1 (en) | 1990-08-23 |
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