METHOD FOR PRODUCING GLASS FIBER

Abstract: A process for making glass fibers comprising supplying a stream of molten glass to a rotating rotor (50); discharging said glass through orifices in said rotor (50) as a plurality of primary streams; and attenuating said primary streams into fibers, said rotor (50) being fabricated from a superalloy by a process comprising hot isostatically pressing the superalloy material sufficient to substantially increase the high-temperature service capability of the rotor (50); and electropolishing said rotor (50) to at least partially remove the sharp edges and discontinuities in the orifices (55) to reduce or eliminate the amount of break-in time otherwise required.

Description: METHOD FOR PRODUCING GLASS FIBER TECHNICAL FIELD The invention disclosed herein relates to the centrifugal production of glass fibers or filaments by post fabrication treatment of the spinner to improve the physical attributes of the spinner ana to improve the quality of the glass filaments produced thereby. BACKGROUND ART The production of glass filaments for use as insulation by the centrifugal or rotory process is well known. Cobalt, nickel , or iron based superalloys can be employed as the material of the rotor, or centrifuge, with cobalt based and nickel based receiving more widespread use because of their superior properties. For example, see U.S. Patent .os. 3,933,484, 3,318,69*4, 3,010,201, 3,980,473, 3,881 ^ ,918, 3,806,338, 3,984,240 and 4,203,747. The requirements for the rotor alloys include nigh temperature strength and creep resistance as well as oxidation resistance and corrosion resistance to molten glass. Unfortunately, the strongest alloys generally exhibit poor corrosion resistance, and the more corrosion resistant alloys are, as a practical matter, limited to service in the fiberization of traditional insulation forming glasses which generally exhibit a low fiberization temperature, i.e., glasses having a liquidus temperature of less than about 971°C (1780°F) and a viscosity of ' about 316 poise at 1Ϊ99°C (2190°F) or less. Further, some of the present rotors exhibits 20-40 hour (or more) break-in period. During the break-in. period, the fibers produced from such spinners are generally brashy and of low quality. Also, an objectionable amount of dust -is produced during the break-in period which, along with the low quality fibers, produce a glass wool mat or pack having a lower thermal resistance than that of a dust free, high quality fiber wool pack. DISCLOSURE OF THE INVENTION This invention pertains to a method of producing glass fibers wherein the spinner employed in a rotary process is subjected to post fabrication treatments of hot isostatic pressing and/or el εctropol i shing to improve the properties and performance of the rotor and to improve the quality of the glass fibers and glass fiber pack produced therefrom. BRIEF DESC IPT10N OF DR HIMGS FIG. 1 is a semi -schemati c , front elevational view of a rotary fiber-forming system for producing glass wool . FIG. 2 is ' an enlarged cross-sectional view of the spinner shown in FIG. 1. FIG. 3* is a photograph of the mi crostructure of a cross-section of a standard or "untreated" spinner. FIG. 4 is a photograph of the mi crostructure of a spinner of the same alloy composition as that shown in FIG. 3 which has been treated by hot isostatic pressing (HIP) according to the principles of this invention. FIG. 5 is a histogram of the fiber diameter distribution produced on a standard spinner after 20 minutes of operation. FIG. 6 is a histogram of the fiber diameter distribution produced by spinner receiving a HIP treatment according to tna principles of this invention after 20 minutes of operation. ' FIG. 7" is a histogram of the fiber diameter distribution produced on a standard spinner after 100 hour.s of operati on . FIG. 8 is a histogram of the fiber diameter distribution produced by spinner receiving a HIP treatment after 100 hours of operation. FIG. 9 is a photograph of a portion of a pack of glass fi rs produced on a standard or untreated spinner af er 15 minutes of operation. FIG. 10 is a photograph of a portion of a mat or pack of glass fibers produced on an el ectropol {shed spinner according to εha principles of this invention after 15 inutes of operation. FIG. 11 is a histogram of the fiber diameter distribution produced on a standard spinner after 15 inut s of operation. FIG. 12 is a nistogram of the fiber diameter distribution produced by a spinner receiving an el ectropol i shing treatment according to the principles of this invention after 15 minutes of operation. BEST MODE OF CARRYING OUT THE I.iVENTIOH As shown in FIG. 1, rotary or centrifugal fiber- forming system 40 is comprised of a flow means or channel 42 having a body of molten inorganic material 44, such as glass, therein. A stream of molten glass 46 is supplied to the rotor or spinner 50 from channel 42, as is known in the art . _ . Spinner 50, which is adapted to be rotated at high speeds is comprised of a quill 52 and a circumferential stream defining or working wall 54 having a plurality of orifices 55 therethrough to supply plurality of pre-fi 1 ament or primary streams of molten and inorganic material to be fiberized. After forming the body of the rotor by any suitable process, such as casting, thousands of noles a re formed in the circumferential wall , for example, by electron beam drilling. In conjunction with rotor 50, a shroud 56 and circumferential blower or fluid attenuation means 57 a r adapted to fluidically assist in the attenuation of the streams of molten material into fibers or filaments 60. A binder material or coating may be applied to the fibers 50 ■ by means of binder applicators 58 as is known in the art. The fibers than may be col lected as a pack or mat to produce "wool" type glass fiber insulation. According to the principles of this invention, spinner 50 receives a post-f brication treatment (i .e., a treatment subsequent to the formation of the thousands of orifices 55 in the circumferential wall 54) of hot isostatic pressing and/or el ec ropol i shing to improve the physical properties and performance of the spinner and/or improve the quality of tne fibers and wool pack produced therefrom. However, it is to be understood that the alloy may be HIP'd prior to the formation of orifices 55, if desired, to achieve the strengthening of the alloy. Ro-tor 50 may be of any of the alloys conventionally employed in a rotary fiber forming process such as a cobalt (Co) based superalloy, or nickel (Hi ) based superalloy or'iron (Fe) based suDεral loy w i ch contain carbon and carbide formers. Exemplary carbide formers are tungsten (W), chromium (Cr), vanadium (Va), tantalum (Ta), hafnium (Hf), zirconium (Zr) and titanium (Ti). Desirably, the rotor is a nickel based superalloy or a cobalt based superalloy with the latter being preferred. The HIP treatment of such superalloys provides a mechanically stronger spinner having greater high-temperature service capability than an un-HIP'd spinner of the same alloy composition. With such improved high-temperature service capab li ies, HIP treated spinners are capable of fiberizing not only traditional insulation forming glasses but also glasses which are of a higher liquidus temperature and of higher viscosity. The service life of un-HIP'd spinners on such higher liquidus glasses is unacceptably brief. In addition to the improved rupture strength and improved creep rate*, thus providing a mechanically stronger spinner, it has been surprisingly found that diameters of the orifices 55 are rendered more uniform by the HIP treatment. Also, the HIP treatment appears to reduce the rate of orifice wear to prolong rotor life, and to a lesser extent, smooths the orifice walls to provide "smoother or less brashy" filaments immediately upon start-up. It is believed that the improved high-temperature strengtn is provided by redistribution of the metallic carbides in the alloys through precipitation hardening. With the simultaneous application of a sufficient amount of heat and pressure during HIP'ing for a sufficient period of time, the metallic carbides precipitate along grain boundaries to provide grain boundary locking to reduce the amount of dislocatiθ-n movement. Merely heating the rotor does not produce tne tigh , ' regular network of precipitated carbides as can be seen in FIG. 4. FIGS. 3 and Δ. are photos of enlarged cross-sections of spinners fabricated from a cobalt ba.sed superalloy containing about 45 cobalt (Co), 31% chromium (Cr), 12?' nickel (N1) and containing lessor amounts of tungsten (W), tantalum (Ta), carbon (C), silicon (Si ), zirconium (Zr), and boron (8). FIG. 3 shows the •■) i cros cructure of an unused and un-HIP'd spinner of such an alloy, and FIG. 4 shows the mi crostructure of an unused spinner after HIP treatment at 1204 U C (2200°F) and 103.42 MPa (15,000 psi ) for two hours. Clearly, a metallurgical change has taken place as a result of the HIP treatment sufficient to increase the mechanical strength and hi gh- emperature service capability of the rotor 50. In general , the pressure applied during the HIP'ing treatment snould be greater than the yield strength of the material at that temperature to render the orifices in the rotor wall more uniform and to provide the strength improvement i n the material its lf. -flJRE - 5 - Regarding the HIP treatment, temperatures within the range from about 1093 to 1204 ϋ C (200Q to 2200 C F) pressures within the range from about 68.95 i_Pa (10,000 psi ) to about 206.84 MPa (30,000 psi), and times of about 1 to about 4 nours are exemplary to produce the metallurgical changes and orifice uniformity improvement heretofore discussed. A HIP temperature of 1177°C (2150 ϋ F), pressure of 103.42 MPa (15,000 psi ) for a period of two hours was employed on a number of spinners to produce the results shown in FIGS. 4 " , 6 and 8 for the aforementioned cobalt based alloy. At the end of the HIP treatment cycle, the HIP chamber is purg-εd of ts working fluid, usually an inert gas such as argon, and tne oxygen containing atmosphere is permitted to enter tne HIP chamber. Since the spinners a still extremely hot, it is believed the oxygen in the air reacts with the surface of the al.loy to form a thin metallic oxid coating thereon, including the walls of the orifices themselves. For example, for the aforementioned cobalt oass ?.lloy, which contains Cr, an oxide of Cr is believed formed, which is less susceptible to the corrosive attack of the molten glass. Regardi ng ' the increase in uniformity of the orificed diameters, FIGS. 5 and 6 show the percent frequency distribution of filaments produced, from traditional insulation forming glasses, after 20 minutes of operation from HIP'd and un-HIP'd spinners of the aforementioned cobalt based superalloy. FIG. 5 shows th ' ε fiber diameter distribution produced from tne untreated spinner. Analysis indicates that the mean fiber diameter collected was 5.9 microns, and the standard deviation therefrom was 4.8 microns. The fiber diameter distribution of the HIP treated spinner is shown in FIG. 6, with a mean fiber diameter of 4.1 microns, and a standard deviation therefrom of 4.3 microns. With each of these spinners being fabricated essentially identical to one another, with the exception of the HIP treatment, it can be seen that the diameter of the fibers - / - 1 produced from the HIP'd spinners are more uniform than the un-HIP'd spinn rs. FIGS. 7 and 8 are simi lar percent frequency histograms of the fiber diameters produced by HIP'd and un-HIP'd spinners after 100 hours of operation employing traditional insulation forming glasses. FIG. 7, shows the fiber distribution produced from standard or un-HIP'd spinner of the aforementioned cobalt base super alloy. The fibers produced therefrom had a mean fiber diameter of 7.64 microns with a standard deviation of 5.13 microns . FIG. 8 shows the fiber distribution of filaments produced on a substantially identical spinner to that represented in FIG. 7, witn the exception of a post-fabrication HIP treatment according to the principles of this invention. The fibers produced therefrom had a mean diameter of 5.69 microns with a standard deviation of 3.75 microns. Once again, the diameter of the fibers produced by the HIP'd spinner are more uniform than the fibers produced on the untreated spinner. Further, measurements of orifice dia eters taken at selected sections along a spinner wall before and after HIP treatment also show that the hole diameters are rendered more uniform as a result of the HIP treatment. Also, orifice diameters were rendered smaller after HIP'ing from about 0.0 cm (0.0") (i .e. , no change) to about 0.00254 cm (0.001"), with an average orifice diameter decrease of about 3?' being observed. Thus, it is believed that fibers having a narrower diameter distribution are produced as represented in the comparisons provided in FIGS. 5 through. 8. It is also interesting to note that the HIP treated • spinners produced fewer larger diameter filaments which accounts in part, at least, for the reduction in the mean fiber diameter for such spinners. Rupture tests conducted on test samples of the aforementioned cobalt based super alloy also show surprising improvements in critical properties for spinner materials. Specimens of un-HIP'd nd HIP'd cobalt based super alloys were individually placed under a tensile load of 20.68 MPa (3,000 psi) at a temperature of 1149°C (2,100°F) and held there until the specimen ruptured. The standard or un-HIP'd specimens had a life of about 32 hours, whereas the HIP treated specimens had a life of about 70 hours. The untreated specimens had a rupture ductility of about 4.2 percent whereas the HIP treated specimens had a rupture ductility of about 6.7 percent. Further, the untreated specimens had a creep rate of 6.6 x -4 10 cm per cm per hour whereas the HIP treated specimens had a creep rate of 4.2 x 10 .- " 4 cm per cm per hour. Further comparisons between un-HIP'd. and HIP'd spinners indicate that after 180 hours of operation on traditional insulation forming glasses, the HIP treated spinners had approximately an 18 percent reduction in hole wear as compared to the standard or un-HIP'd spinners of the aforementioned cobalt base superalloy. Such a reduction in hole wear may be based in part on the - toughening of the metal itself and in part based upon the formation of an oxide coating on the alloy surface as a result of the HIP treatment process as discussed previously herein. Surprisingly, the k-valu. or thermal conductance of the insulation pack produced by the HIP treated spinner is lower than that produced by the un-HIP'd spinner. An explanation may be found in the fact that for the HIP'd spinner the fiber distribution parameter or X (which actually is the standard deviation from the mean fiber diameter) has a lower .value. This reduces the equivalent radiation conductivity k rad for the pack. 1 A + B k rad φ 2 + where A, 8 are constants r° is the pack density is the mean fiber diameter "/ is the fiber distribution parameter FIGS. 5 through 8 clearly indicate that for the HIP'd spinner, " ) πas a lower value. The use of electropoli shing as a post-fabrication treatment (i .e., after the orifices 55 are formed in rotor 50) has been shown to (a) virtually eliminate any break-in period normally associated with such spinners and to (b) provide a glass fiber pack of improved quality. Electropolis ing, hic is the opposite of the el ctropl ting process, is particularly effective since electropolishing pref rentially attacks or dissolves the sharp edges or discontinuities in the orifices or at the edges of the orifices, which occur as a result of the orifice formation process. A spinner composed of the aforementioned cobalt base superalloy having a preselected number of orifices formed therein, was placed in a polyethylene electrolytic cell having a stainless steel cathode ring and a stainless steel anode disk in contact with the spinner, thus making t e spinner the anode, in the electrolytic circuit. The electrolytic cell as suitably filled ith an electrolyte composition of 75.7 percent (by volume) thonol , 15.15 percent phosphoric acid (H3 O4), and 9.09 percent sulfuπ ' c acid (H ? S0. ) , and energized to suitably polish the orifices of the spinner. Current density is desirably held within ~ 2 the range from about 0.11 amps/cm ~ to about 0.14 amp/cm for about 30 minutes. Typically, times may vary, but they usually fall within the range from about 10 minutes to about 50 minutes for suitable polishing to take place. As a preparatory step to the electropolishing treatment itself, the spinner s ould be t oroughly cleaned of any residue and/or foreign material by means of solvent washing and/or vapor honing and the like to achieve the maximum electropolishing rate. At fiberization start-up, the el setropol i shed spinners immediately began producing glass fibers having a surface smoothness or texture similar to that produced by seasoned spinners, without the electropolish ng treatment. It is known that new standard or untreated spinners generally produce mats of glass fibers having a brasny feel. Such an undesirable brashy feel dissipates as the spinner is seasoned during operation. In addition, the el ectropol shed spinners produced a pack of fibers that has a significantly reduced dust content as compared to unpolished, new spinners. FIG. 9 is a pn to of a mat or pack of glass fibers produced from a standard or untreated spinner after 15 minutes of operation. It is clear ^ that there are a number of ultraf-ine fibers in the pack, a number of which are fused or bonded to tne surface of the larger diameter fi bεrs . FIG. 10 is an enlarged photo of a Dack of glass fibers produced on a spinner after receiving the post fabrication electropol shing treatment. Clearly, the number of ultrafine filaments is substantially reduced. Regarding the spinners associated with FIGS. 9-12, such soinners were of the aforementioned cobalt-based superalloy, and the photos and histograms are based upon samples taken approximately after 15 minutes of operation. FIG. 11 is a histogram of the percent frequency distribution of the filament diameters produced by standard or untreated spinner, ana FIG. 12 is a Histogram of the percent frequency distribution of the filament diameters produced by an electπopo I i shed spinner according to the principles of this invention. -As can be seen therein, the percentage of the fibers having a diameter of 1 micron or less, (i .e. those in the submicron range) are substantially reduced. Also, the number of filaments in the range from 0 to 3 microns are also substantially reduced. Analysis of the samples from the standard spinner indicates the fibers exhibited a mean diameter of 7.4 microns and a standard deviation therefrom of 5.62 microns. Tne fibers produced from the el ectroDol shed spinner exhibited a mean filament diameter of 6.94 microns with a standard deviation therefrom of 5.04 microns. With regard to the number of filaments in the submicron range, or those filaments having a diameter of 1 micron or less, an analysis of product samples indicates that the standard spinners produce a wool pack having submicron filaments which comprise from about 2 to about 4 . percent of the mat or pack. The electropolished spinners, however, produced a pack of glass fibers having from about .4 to about 2.8 percent filaments in the sub i cron range . Additionally, the standard spinner produced a pack of glass fibers having from about 18.8 to about 27.3 percent filaments having a diameter of 3 microns or less. The electropolished spinner produced a pack of glass fibers naving from about 15.3 to about 25.2 percent filaments having a diameter of 3 microns or less. With the reduction of the percentage of ultrafine filaments, and, more importantly, those in the submicron range, t e pack does not exhibit the same brashy feel to the touch as exhibited by the untreated spinner at startup. Further, the reduction of the ultrafine and submicron diameter filaments contributes in large part to the reduction in the "dust" produced by untreated spinners. Thus, the quality of t e glass fila ents and pack produced from such spinners is surprisingly and significantly improved by the application of an electropolishing treatment to the fabricated spinner prior to operation of the spinner for the production of fibers. As a result of the smooth, hi g.i-qual i ty fibers and the reduced dust content, the k-value of the insulation pack is also decreased since the fiber distribution parameter is decreased as a result of the electropolishing treatment. Thus, the thermal resistance of the pack increased as compared to a pack produced employing non-el ectropol i shed spinners. The not isostatic pressing treatment and the el ectropol ' ishing treatment may be used alone or desirably in combination with one another to achieve tne various benefits noted herein. When combining the hot isostatic pressing ' with the electropolish.ing treatment, it is preferred that the electropolishing treatment precede the HIP'ing treatment for maximum benefit. Otherwise, the surface d scon inuities and sharp edges may be more difficult to remove by electropolishing if the HIP'ing treatment precedes the electropolishing treatment. It is apparant that, within the scope of the present invention, modifications of different arrangements can be made otπer than as herein disclosed. The present disclosure is merely illustrative with the invention comprehending all variations thereof. INDUSTRIAL APPLICABILITY The invention described herein is readily applicable to the glass fiber industry. f MPI

Claims: _ 1 "• C U I H S 1. In a metnod of making glass fibers comprising; supplying a stream of molten glass to a rotating rotor; discharging Said glass througn orifices in said rqtor as a plurality of primary streams; and attenuating said primary streams into fibers, the improvement comprising electropolishing said rotor sufficient to substantially reduce the percentage of ultrafine fibers produced therefrom. 2. The metnod of claim 1 wherein the orifices a n formed n saiα rotor by electron beam drilling and wherein said electropolishi g pref rentially at least partially dissolves the sharp edges and splatter in the orifices produced by sucn drilling. 3. The mέthoα of claim 1 herein the number of ultrafine filaments fusod to larger diameter filaments at start-up of fiberization is reduced as compared to a non-el ectropol i shed rotor. 4. The method of claim 1 furtner comprising collecting said fibers as a pack, wherein said .1 ectropol i shi ng is effective to increase the thermal resistance of the pack of glass fibers produced therefrom. 5. The method of claim 1 further comprising hot isostatical ly pressing said rotor material sufficient to substantially increase the high temperature service capability of the rotor, said rotor being fabricated from a superal 1 o . 6. The method of claim 5 wherein said superalloy material is a carbon containing superalloy selected from OMPI the group consisting of Co, Ni and Fe based alloys and wherein said superalloy also includes carbide formers. 7. The method of claim 5 wherein tne temperature and pressure of the hot isostatic pressing a re sufficient to effect the redistribution of the metallic carbides in the alloys through precipitation hardening to provide grain boundary locking. 8. The method of claim 7 wherein said orifices are formed in said rotor prior to said hot isostatic pressing step. 9. The method of claim 7 wherein said electropolishing step is carried out subsequent to said hot isostatic pressing step. 10. In a method of making glass fibers comprising; supplying a stream of molten glass to a rotating rotor; discharging said glass through orifices in said rotor as a plurality of primary streams; and attenuating said primary streams into fibers, said spinner being fabricated from a superalloy; the improvement comprising hot isostatical y pressing said superalloy material sufficient to substanti lly increase the high temperature servi ce 'capab 1 i ty of the rotor. 11. The method of claim 10 wherein said superalloy material is a carbon containing superalloy selected frdn the group consisting of Co, Ni and Fe based alloys and wherein said superalloy also includes carbide formers . 12. The method of claim 10 wnerein the temperature and pressure of the hot isostatic pressing are sufficient to effect the redistribution of the metallic carbides in the alloys through precipitation hardening to provide grain boundary locking. 13. The method of claim 10 wherein said orifices are formed in said rotor prior to said hot isostatic pressing step. 14. The method of claim 10 wherein said hot isostatic pressing is conducted at a temperature within the tetrxr range from about 1093 to 1204°C (2000 to 2200°F); at a pressure from aDout 68.95 MPa (10,000 psi ) to about 206.84 MPa (30,000 psi ); for a period from about 1 to about 4 hours .

Inventors: BHATTI MOHINDER SINGH, BHATTI, MOHINDER, SINGH
Applicants: OWENS CORNING FIBERGLASS CORP, OWENS-CORNING FIBERGLAS CORPORATION
Application year: 1984
Main classification: C03B37
IPC codes: C03B37