Method for producing a fibre-composite made from amorphous, chemically modified polymers with reinforcement fibres

Abstract

The invention relates to a method for producing a thermoplastic fibre composite containing a thermoplastic moulding compound (A) as a polymer-matrix (M), reinforcement fibres (B), and optionally additive (C). Said method comprises the following steps: i) flat structures (F) made from reinforcing fibres (B) treated with a silane sizing material are provided, ii) the flat structures (F) are placed in a thermoplastic molding compound (A) which comprises at least 0.3 mol %, with respect to components (A), of a chemically reactive functionality, iii) chemically reactive groups of the thermoplastic molding compound (A) are reacted in the polymer matrix (M) with the polar groups of the treated reinforcing fibres (B), iv) the at least one additive (C) is optionally incorporated v) cooling. Said method is particularly suitable for producing fibrous composites.

Claims

1. A process for producing a thermoplastic fiber composite material comprising a thermoplastic molding compound A as polymer matrix M, treated reinforcing fibers B, and optionally at least one additive C, comprising the steps of: i) providing sheetlike structures F which are composed of reinforcing fibers B, treated with a silane size, and selected from the group consisting of weaves, mats, nonwovens, scrims and knits, ii) introducing the sheetlike structures F into a thermoplastic molding compound A having at least 0.3 mol%, based on the thermoplastic molding compound A, of a chemically reactive functionality in the form of functional monomers comprising one or more chemically reactive groups, iii) reacting chemically reactive groups in the thermoplastic molding compound A as the polymer matrix M with polar groups at the surface of the treated reinforcing fibers B, iv) optionally incorporating at least one additive C and consolidating the thermoplastic fiber composite material, and v) cooling and optionally further process steps, wherein the sheetlike structures F permeate more than 50% of the area of the thermoplastic fiber composite material in two of three spatial directions.

2. The process for producing a thermoplastic fiber composite material as claimed in claim 1, wherein the fiber composite material is produced from a) 30% to 95% by weight of the thermoplastic molding compound A as polymer matrix M, b) 5 to 70% by weight of the sheetlike structures F composed of reinforcing fibers B, and c) 0 to 40% by weight of additive C.

3. The process for producing a thermoplastic fiber composite material as claimed in claim 1, wherein the thermoplastic molding compound A used as polymer matrix M is amorphous and is selected from the group of copolymers modified by a chemically reactive functionality that are based on: styrene-acrylonitrile copolymers, alpha-methylstyrene-acrylonitrile copolymers, impact modified acrylonitrile-styrene copolymers, and blends of the copolymers mentioned with polycarbonate or polyamide.

4. The process for producing a thermoplastic fiber composite material as claimed in claim 1, wherein the thermoplastic molding compound A consists of copolymers selected from the group consisting of styrene-acrylonitrile copolymers and alpha-methylstyrene acrylonitrile copolymers that have been modified by a chemically reactive functionality.

5. The process for producing a thermoplastic fiber composite material as claimed in claim 1, wherein the chemically reactive functionality of the thermoplastic molding compound A is based on components selected from the group consisting of: maleic anhydride, N-phenylmaleimide, and glycidyl (meth)acrylate.

6. The process for producing a thermoplastic fiber composite material as claimed in claim 1, wherein the surface of the reinforcing fibers B comprises one or more of the functions from the group of hydroxyl, ester, and amino groups as the polar groups of the treated reinforcing fibers B.

7. The process for producing a thermoplastic fiber composite material as claimed in claim 1, wherein the thermoplastic compound A is produced using 0.5% to 5% by weight of monomers A-I, based on the thermoplastic compound A, which have a chemically reactive functionality.

8. The process for producing a thermoplastic fiber composite material as claimed in claim 1, wherein the thermoplastic compound A is prepared from 65% to 80% by weight of (-methyl)styrene, 19.7% to 32% by weight of acrylonitrile, and 0.3% to 3% by weight of maleic anhydride as the chemically reactive functionality.

9. The process for producing a thermoplastic fiber composite material as claimed in claim 1, wherein the reinforcing fibers B consist of glass fibers comprising silanol groups as the polar groups of the treated reinforcing fibers B on the surface.

10. The process for producing a thermoplastic fiber composite material as claimed in claim 1, wherein the fiber composite material has a ribbed structure or a sandwich structure.

11. The process for producing a thermoplastic fiber composite material as claimed in claim 1, wherein the fiber composite material has a layered structure and comprises more than two layers.

12. The process for producing a thermoplastic fiber composite material as claimed in claim 1, wherein the temperature in the production of the fiber composite material is at least 200 C. during procedural steps (ii) and (iii).

13. The process for producing a thermoplastic fiber composite material as claimed in claim 1, wherein the residence time in the production of the fiber composite material at temperatures of at least 200 C. is not more than 10 minutes during procedural steps (ii) and (iii).

14. The process for producing a thermoplastic fiber composite material as claimed in claim 1, wherein the thermoplastic molding compound A is produced from at least 65% by weight of (-methyl)styrene, 19.9% to 32% by weight of acrylonitrile, and 0.3% to 2% by weight of maleic anhydride as the chemically reactive functionality, and wherein the residence time for production of the fiber composite material at temperatures of at least 200 C. is not more than 10 minutes during procedural steps (ii) and (iii).

15. A thermoplastic fiber composite material produced by the process of claim 1.

16. A molding, film or coating comprising the thermoplastic fiber composite material as claimed in claim 15.

17. The process for producing a thermoplastic fiber composite material as claimed in claim 1, wherein the thermoplastic molding compound A used as polymer matrix M is amorphous and is selected from the group of copolymers modified by a chemically reactive functionality that are based on: impact modified acrylonitrile-styrene copolymers selected from acrylonitrile-butadiene -styrene copolymers and acrylonitrile-styrene-acrylic ester copolymers.

18. The process for producing a thermoplastic fiber composite material as claimed in claim 1, wherein the thermoplastic molding compound A consists of copolymers selected from the group consisting of styrene-acrylonitrile copolymers and alpha-methylstyrene acrylonitrile copolymers that have been modified by the chemically reactive functionality maleic anhydride (MA).

Description

FIGURES

(1) FIG. 1 shows the fiber composite materials W which have been obtained according to experiment no. 1. FIG. 1A shows the visual documentation. FIG. 1B shows the microscope view of a section through the laminar fiber composite material W arranged in horizontal alignment (on the left: 25-fold magnification, on the right: 50-fold magnification), the fibers being clearly apparent as a horizontal dark-colored layer between the light-colored layers of thermoplastic molding compound. FIG. 1C shows the 200-fold magnification, it being apparent that the impregnation is incomplete at some points.

(2) FIG. 2 shows the fiber composite materials W which have been obtained according to experiment no. 2. FIG. 2A shows the visual documentation. FIG. 2B shows the microscope view of a section through the laminar fiber composite material W arranged in horizontal alignment (on the left: 25-fold magnification, on the right: 50-fold magnification), the fibers being clearly apparent as a horizontal dark-colored layer between the light-colored layers of thermoplastic molding compound. FIG. 2C shows the 200-fold magnification, it being apparent that the impregnation is partially incomplete.

(3) FIG. 3 shows the fiber composite materials W which have been obtained according to experiment no. 3. FIG. 3A shows the visual documentation. FIG. 3B shows the microscope view of a section through the laminar fiber composite material W arranged in horizontal alignment (on the left: 25-fold magnification, on the right: 50-fold magnification), with no apparent layer of fibers. FIG. 3C shows the 200-fold magnification, it being apparent that the impregnation is substantially complete.

(4) FIG. 4 shows the fiber composite materials W which have been obtained according to experiment no. 4. FIG. 4A shows the visual documentation. FIG. 4B shows the microscope view of a section through the laminar fiber composite material W arranged in horizontal alignment (on the left: 25-fold magnification, on the right: 50-fold magnification), with no apparent layer of fibers. FIG. 4C shows the 200-fold magnification, it being apparent that the impregnation is incomplete at individual points.

(5) FIG. 5 shows the fiber composite materials W which have been obtained according to experiment no. 5. FIG. 5A shows the visual documentation. FIG. 5B shows the microscope view of a section through the laminar fiber composite material W arranged in horizontal alignment (on the left: 25-fold magnification, on the right: 50-fold magnification), with no apparent layer of fibers. FIG. 4C shows the 200-fold magnification, it being apparent that the impregnation is incomplete at a few points.

(6) FIG. 6 shows the production of the fiber composite materials W (here: glass fiber weave) in the press intake V25-V28. It is clearly apparent that a production process of this kind permits continuous production. Moreover, it is apparent via the embossment of the pattern that the fiber composite material W is also three-dimensionally formable.

(7) FIG. 7 shows, in schematic form, the development of undesired formation of surface waves (texture).

EXAMPLES

(8) The experiments which follow were conducted in an intermittent hot press capable of producing a fiber/film composite from polymer film, melt or powder, for quasi-continuous production of fiber-reinforced thermoplastic semifinished products, laminates and sandwich sheets.

(9) Sheet width: 660 mm

(10) Laminate thickness: 0.2 to 9.0 mm

(11) Laminate tolerances: max.0.1 mm corresponding to semifinished product

(12) Sandwich sheet thickness: max. 30 mm

(13) Output: about 0.1-60 m/h, depending on quality and component thickness

(14) Nominal advance rate 5 m/h

(15) Mold pressure: compression unit 5-25 bar, infinitely adjustable for minimum and

(16) maximum mold size (optional)

(17) Mold temperature control: 3 heating zones and 2 cooling zones

(18) Mold temperature: up to 400 C.

(19) Mold length: 1000 mm

(20) Press opening distance: 0.5 to 200 mm

(21) Technical Data of the Melt Plastification are:

(22) Discontinuous melt discharge in center position for production of fiber-reinforced thermoplastic semifinished products:

(23) Screw diameter: 35 mm

(24) Max. stroke volume: 192 cm.sup.3

(25) Max. screw speed: 350 rpm

(26) Max. discharge flow rate: 108 cm.sup.3/s

(27) Max. discharge pressure: 2406 bar (specific)

(28) Flexural stress and flexural modulus were determined according to DIN 14125:2011-05.

(29) Components:

(30) A1: styrene-acrylonitrile (S/AN) copolymer with the following composition: 75% by weight styrene (S) and 25% by weight acrylonitrile (AN), viscosity number 60, Mw 250 000 g/mol (measured via gel permeation chromatography on standard columns with monodisperse polystyrene calibration standards) A2: S/AN/maleic anhydride (MSA) copolymer with the composition (% by weight): 74/25/1; concentration of functional groups: 1% by weight of MA (98.1 g/mol) in 74% by weight of styrene (104.2 g/mol) and 25% by weight of AN (53.1 g/mol), Mw 250 000 g/mol (measured via gel permeation chromatography on standard columns with monodisperse polystyrene calibration standards) A3: mixture of A2:A1=2:1, concentration of functional groups: 0.67% by weight of MA A4: mixture of A2:A1=1:2, concentration of functional groups: 0.33% by weight of MA B1: bidirectional glass fiber scrim 0/90 with basis weight=approx. 590 g/m.sup.2, weft+warp=1200 tex (=1200 g/1000 m)[for example KN G 590.1 from P-D Glasseiden GmbH] B2: glass fiber twill weave 2/2 with basis weight=approx. 576 g/m.sup.2, weft+warp=1200 tex [for example GW 123-580K2 from P-D Glasseiden GmbH]

(31) The combinations and parameter settings for the process described in claim 1 are listed in the following table:

(32) TABLE-US-00001 TABLE 1 Compositions of comp. 1, comp. 2, comp. 10 and comp. 15 and of the inventive compositions V3 to V9 and V11 to V14. No. A1 A2 A3 A4 B1 B2 T [ C.] t [s] Comp. 1 X X 260 20-30 Comp. 2 X X 300 30-30 V3 X X 280 20-30 V4 X X 280 40 V5 X X 320 30-30 V6 X X 300 20-30 V7 X X 320 20-30 V8 X X 310 20-30 V9 X X 320 20-30 Comp. 10 X X 320 20-30 V11 X X 320 20-30 V12 X X 320 20-30 V13 X X 320 20-30 V14 X X 320 20-30 Comp. 15 X X 320 20-30 X: proportion by weight of component A:B = 60:40

(33) Table 1 shows the conditions in the experiments conducted.

(34) In this context, the reactants and the temperature and pressing time were varied. The pressure in all the test series was about 20 bar.

(35) TABLE-US-00002 TABLE 2 Mean values for maximum flexural stress in warp and weft direction for the organosheets produced according to the mixtures comp. 2, V5, V7, V9, comp. 10, V12 to V14 and comp. 15, with a production temperature in each case of at least 300 C. Mean values for maximum No. Fiber direction flexural stress [MPa] Comp. 2 warp direction 211.23 weft direction 184.94 V5 warp direction 670.48 weft direction 271.05 V7 warp direction 590.98 weft direction 301.21 V9 warp direction 371.73 weft direction 244.62 Comp. 10 warp direction 319.8 weft direction 236.01 V12 warp direction 556.15 weft direction 484.24 V13 warp direction 528.96 weft direction 386.83 V14 warp direction 513.95 weft direction 413.86 comp. 15 warp direction 423.03 weft direction 301.40

(36) The values shown in table 2 are the mean value of 9 measurements in each case. Table 2 shows that the inventive organosheets V5, V7, V9, V12, V13 and V14 have a higher mean maximum flexural stress than the organosheets having a matrix comprising 75% by weight of styrene (S) and 25% by weight of acrylonitrile (AN) (comp. 10 and comp. 15). The comparison of V9 with comp. 10 also shows that, under the same conditions (T=320 C. and t=30 s), the organosheet of the invention has greater flexural stress both in warp direction and in weft direction.

(37) It is found that the process for producing the fiber composite material with a thermoplastic molding compound A and reinforcing fibers B can give improved products.

(38) Further Examination of Multilayer Fiber Composite Materials

(39) Technical Data of the Intermittent Hot Press (IVHP):

(40) Quasi-continuous production of fiber-reinforced semifinished products, laminates and sandwich sheets

(41) Sheet width: 660 mm

(42) Laminate thickness: 0.2 to 9.0 mm

(43) Laminate tolerances: max.0.1 mm corresponding to semifinished product

(44) Sandwich sheet thickness: max. 30 mm

(45) Output: about 0.1-60 m/h, depending on quality and component thickness Nominal advance rate 5 m/h

(46) Mold pressure: press unit 5-25 bar, infinitely adjustable for minimum and maximum mold size (optional)

(47) Mold temperature control: 3 heating and 2 cooling zones

(48) Mold temperature: up to 400 C.

(49) Mold length: 1000 mm

(50) Press opening distance: 0.5 to 200 mm

(51) Production direction: from right to left

(52) Technical Data of the Melt Plastification:

(53) Discontinuous melt discharge in center position for production of fiber-reinforced thermoplastic semifinished products:

(54) Screw diameter: 35 mm

(55) Max. stroke volume: 192 cm.sup.3

(56) Max. screw speed: 350 rpm

(57) Max. discharge flow rate: 108 cm.sup.3/s

(58) Max. discharge pressure: 2406 bar (specific)

(59) Here:

(60) Melt volume: 22 ccm

(61) isobaric=pressure-controlled pressing operation

(62) isochoric=volume-control pressing operation

(63) T [ C.]=temperature of the temperature zones* (*the press has 3 heating and 2 cooling zones, specified in production direction)

(64) p [bar]=pressure per cycle: isochoric 20

(65) s [mm]=distance limit for compression thickness: 1.1 mm

(66) Temperature profile: (i) 210 to 245 C., so about 220 C.

(67) (ii) 300 to 325 C., so about 300 C. (iii) 270 to 320 C., so about 280 to 320 C. (iv) 160 to 180 C. (v) 80 C.
t [sec]=pressing time per cycle: 20-30 s
Construction/lamination: 6-ply construction with middle melt layer; production process: direct melt (SD)
Matrix Components A:
M1 (SAN type): styrene-acrylonitrile-maleic anhydride (SAN-MA) terpolymer (S/AN/MA: 74/25/1) with an MA content of 1% by weight and an MVR of 22 cm.sup.3/10 min at 220 C./10 kg (measured to ISO1133);
M1b corresponds to the aforementioned component M1, with an additional 2% by weight of industrial black mixed into the matrix.
M2 (SAN type): styrene-acrylonitrile-maleic anhydride (SAN-MA) terpolymer (S/AN/MA: 73/25/2.1) with an MA content of 2.1% by weight and an MVR of 22 cm.sup.3/10 min at 220 C./10 kg (measured to ISO1133);
M2b corresponds to the aforementioned component M2, with an additional 2% by weight of industrial black mixed into the matrix.
M3 (SAN type): blend of 33% by weight of M1 and 67% by weight of the SAN copolymer Luran VLN, so 0.33% by weight of maleic anhydride (MA) in the overall blend;
M3b corresponds to the aforementioned component M3, with an additional 2% by weight of industrial black mixed into the matrix.
PA6: semicrystalline, free-flowing polyamide Durethan B30S
PD(OD): free-flowing amorphous optical grade polycarbonate for optical discs;
Fiber Components B:
Glass filament twill weave (brief designations: GF-KG(LR) or LR), 2/2 twill weave, basis weight 290 g/m.sup.2, EC9 68 tex rovings, TF-970 finish, supply width 1000 mm (type: 01102 0800-1240; manufacture: Hexcel, obtained from: Lange+Ritter)
Glass filament twill weave (brief designations: GF-KG(PD) or PD), 2/2 twill weave, basis weight 320 g/m.sup.2, 320 tex rovings, 350 finish, supply width 635 mm (type: EC14-320-350, manufacturer and supplier: PD Glasseide GmbH Oschatz)
Glass filament scrim (brief designations: GF-GE(Sae) or Sae) 0/45/90/45, basis weight 313 g/m.sup.2, 300 tex main rovings, PA size finish, supply width 655 mm (type: X-E-PA-313-655, no. 7004344, manufacturer and supplier: Saertex GmbH & Co. KG)
Sae n.s.=300 g/m.sup.2 glass filament scrim, manufacturer designation: Saertex new sizing, +45/45/+45/45
Glass fiber nonwoven (brief designation: GV50), basis weight 50 g/m.sup.2, fiber diameter 10 m, supply width 640 mm (type: Evalith S5030, manufacturer and supplier: Johns Manville Europe)
Visual Assessment

(68) All the fiber composite materials produced were producible in each case as flat organosheets (with a large area) in a continuous process, and it was possible without any problem to cut these to size (in laminatable, customary transport dimensions, for instance 1 m0.6 m). In the case of the transparent fiber composite materials, the embedded fiber material was just apparent on detailed backlit inspection. In the case of the fiber composite materials with a (black-)colored matrix, the embedded fiber material was not/barely apparent even on closer backlit visual inspection.

(69) Microscope Assessment

(70) In this case, defects (craters, dips, etc.) were assessed via epiluminescence microscopy, and the surface quality via confocal laser scanning microscopy (LSM). By means of LSM, a top view of a three-dimensional (3D) survey (7.2 mm7.2 mm) of the local measurement region and a two-dimensional (2D) representation of the differences in height after scaling and use of various profile filters were created. Measurement errors and general distortion/skewness of the sample were compensated for by the use of profile filters (noise filters and tilt filters). The 2D high profile of the image was converted to line profiles via defined measurement lines by integrated software and evaluated with computer assistance.

(71) Fiber composite materials each having four plies of the appropriate sheetlike structure of fibers (GF-KG(PD)(4) or Sae(4) here) embedded into the respective matrix were produced. In order to further increase the comparability of the samples, a thin glass fiber nonwoven (GV50, see above) was applied to each side of the fiber composite materials produced. This had no noticeable effect on the mechanical properties.

(72) The mean wave depth (MW Wt) and the median roughness (Ra) were ascertained for numerous fiber composite materials. It was found that the MW Wt for all fiber composite materials in which the matrix comprises a functional component that can react with the fibers is distinctly <10 m, whereas in the case of fiber composite materials with comparable PA6 and PD(OD) matrices it is distinctly <10 m. The median roughness values ascertained were also much less for fiber composite materials of the invention. This is shown by way of example by the measured values below.

(73) TABLE-US-00003 TABLE 3 Test results of the LSM analysis with SAN matrix system - wave depth (Wt) and median roughness (Ra) SAN(1) PC(1) PA6(1) Construction +GF-KG(PD)(4) Components M1b + M2 + M2b + M3b + PC(OD) + PA6 + PD PD PD PD PD PD MW Wt 7.141 7.187 5.181 5.425 11.745 12.323 MW Ra 3.995 4.415 4.17 3.451 6.406 4.968

(74) This likewise became clear when a scrim (such as Sae) was used in place of the weave:

(75) TABLE-US-00004 TABLE 4 Test results of the LSM analysis with SAN matrix system- wave depth (Wt) and median roughness (Ra) Construction SAN(1) PA6(1) Construction +Sae(4) Components M1b + Sae M2b + Sae MW Wt 5.535 5.205 17.05 MW Ra 4.261 4.24 4.861

(76) In further tests, strength in warp direction and in weft direction was examined separately. It was shown that the fiber composite materials are very stable both in warp direction and in weft direction. The fiber composite materials are generally even more stable in warp direction than in weft direction.

(77) Mechanical Properties

(78) Matrix Components A

(79) The matrix components A are as described above.

(80) Fiber Components B (if not Described Above)

(81) FG290=glass filament weave 290 g/m.sup.2, manufacturer designation: Hexcel HexForce 01202 1000 TF970

(82) FG320=glass filament weave 320 g/m.sup.2, manufacturer designation: PD Glasseide GmbH Oschatz EC14-320-350

(83) Sae=MuAx313, glass filament scrim 300 g/m.sup.2, manufacturer designation: Saertex X-E-PA-313-655

(84) Sae n.s.=glass filament scrim 300 g/m.sup.2, manufacturer designation: Saertex new sizing, +45/45/+45/45

(85) Number of layers (for example 4x=four layers of the respective fiber scrim or of the respective fibers)

(86) The transparent fiber composite materials which follow were produced, into each of which was introduced flat fiber material. The fiber composite materials produced each had a thickness of about 1.1 mm. In order to further increase the comparability of the samples, a thin glass fiber nonwoven (GV50, see above) was applied to each side of the fiber composite materials produced. This has no noticeable effect on the mechanical or optical properties. For the samples, the following flexural strengths were ascertained according to DIN EN ISO 14125:

(87) TABLE-US-00005 TABLE 5 Transparent fiber composite materials - flexural strength Glass Modulus Con- content Thickness of Flexural No. struction [g/m.sup.2] Matrix [mm] elasticity strength F/T_1 4xFG290 1260 M2 1.09 18.41 658.89 F/T_2 4xFG320 1380 M2 1.09 18.17 634.32 F/T_3 4xSae 1352 M2 1.16 18.44 444.33 F/T_4 Sae n.s. M2 1.17 15.93 621.04 F/T_5 4xFG320 1380 PC(OD) 1.14 23.36 377.97

(88) Additionally produced were the black-colored fiber composite materials which follow, in which 2% by weight of industrial black was mixed into the matrix and into each of which flat fiber material was introduced. The fiber composite materials produced each had a thickness of about 1.1 mm. In order to further increase the comparability of the samples, a thin glass fiber nonwoven (GV50, see above) was applied to each side of the fiber composite materials produced. This has no noticeable effect on the mechanical or optical properties. For the samples, the following flexural strengths were ascertained according to DIN EN ISO 14125:

(89) TABLE-US-00006 TABLE 6 Nontransparent fiber composite materials - flexural strength Glass Modulus Con- content Thickness of Flexural No. struction [g/m.sup.2] Matrix [mm] elasticity strength F/S_1 4xFG290 1260 M2 1.07 21.61 661.73 F/S_2 4xFG320 1380 M2 1.20 22.70 673.99 F/S_3 4xSae 1352 M2 1.15 14.92 385.21 F/S_4 4xSae 1352 PA6 1.13 14.30 477.77 F/S_5 4xFG320 1380 PA6 1.11 16.95 471.97

(90) In summary, it is found that the weaves used (FG290 and FG320) can be processed to give fiber composite materials having particularly high flexural strength. The fiber composite materials of the invention in which the matrix comprises a component that reacts with the fibers (here: maleic anhydride (MA)) have a significantly higher flexural strength than comparative molding compounds without any such component, for instance PC(OD) or PA6.

(91) By comparison, for the noninventive Luran 378P G7 fiber composite material reinforced with short glass fibers, only a flexural strength of 150 MPa was found, and so a much lower flexural strength.

(92) In addition, for the fiber composite materials, the impact resistance or penetration characteristics (dart test according to ISO 6603) were ascertained. Here too, the fiber composite materials showed a high stability of Fm>3000 N.

(93) Optional Further Processing

(94) It was also shown experimentally that the fiber composite materials obtained had good formability to give three-dimensional semifinished products, for example to give semifinished products in half-shell form. It was additionally shown that the fiber composite materials obtained were printable and laminatable.

(95) Summary of the Experimental Results

(96) The evaluation of different glass fiber-based textile systems with different matrix systems to give a fiber composite material (organosheet) showed that good fiber composite materials (as organosheets and semifinished products produced therefrom) can be produced in a reproducible manner. These can be produced in colorless or colored form. The fiber composite materials showed good to very good optical, tactile and mechanical properties (for instance with regard to their flexural strength and puncture resistance). In mechanical terms, the weaves showed somewhat greater strength and stiffness than scrims. The styrene copolymer-based matrices (SAN matrices) tended to lead to better fiber composite materials in terms of the mechanical indices than the alternative matrices such as PC and PA6. The fiber composite materials of the invention were producible in a semiautomatic or fully automatic manner by means of a continuous process. The fiber composite materials (organosheets) of the invention have good formability to give three-dimensional semifinished products.