U.S. patent application number 13/705577 was filed with the patent office on 2015-05-14 for process for producing a highly transparent impact-resistant glass ceramic.
The applicant listed for this patent is Kurt Schaupert, Ulrich Schiffner, Friedrich Siebers, Thilo Zachau. Invention is credited to Kurt Schaupert, Ulrich Schiffner, Friedrich Siebers, Thilo Zachau.
Application Number | 20150128646 13/705577 |
Document ID | / |
Family ID | 50824093 |
Filed Date | 2015-05-14 |
United States Patent
Application |
20150128646 |
Kind Code |
A9 |
Zachau; Thilo ; et
al. |
May 14, 2015 |
Process for producing a highly transparent impact-resistant glass
ceramic
Abstract
The process for producing a transparent lithium aluminosilicate
glass ceramic plate includes ceramicizing a green glass body of the
Li.sub.2O--Al.sub.2O--SiO.sub.2 system using a ceramization
program, which includes heating it, for the purpose of nucleation,
to a temperature of 750.degree. C..+-.20.degree. C. and maintaining
the temperature for 20.+-.15 minutes, further heating the green
glass body, for the purpose of ceramization, to a temperature of
900.+-.20.degree. C. and maintaining the to temperature for
20.+-.15 minutes and then cooling to room temperature. The
transparent plate has a thermal expansion coefficient (CTE) from
-0.15.times.10.sup.-6/K to +0.15.times.10.sup.-6/K at 30 to
700.degree. C. and a brightness value observed at an angle of
2.degree. of .gtoreq.80 for a 4-mm thick plate for transmitted
normal light.
Inventors: |
Zachau; Thilo; (Bensheim,
DE) ; Siebers; Friedrich; (Nierstein, DE) ;
Schiffner; Ulrich; (Mainz, DE) ; Schaupert; Kurt;
(Hofheim, DE) |
|
Applicant: |
Name |
City |
State |
Country |
Type |
Zachau; Thilo
Siebers; Friedrich
Schiffner; Ulrich
Schaupert; Kurt |
Bensheim
Nierstein
Mainz
Hofheim |
|
DE
DE
DE
DE |
|
|
Prior
Publication: |
|
Document Identifier |
Publication Date |
|
US 20140150500 A1 |
June 5, 2014 |
|
|
Family ID: |
50824093 |
Appl. No.: |
13/705577 |
Filed: |
December 5, 2012 |
Related U.S. Patent Documents
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Application
Number |
Filing Date |
Patent Number |
|
|
12616982 |
Nov 12, 2009 |
8404350 |
|
|
13705577 |
|
|
|
|
Current U.S.
Class: |
65/33.8 |
Current CPC
Class: |
B32B 17/10119 20130101;
C03C 10/0027 20130101; B32B 2333/12 20130101; F41H 5/0407 20130101;
B32B 17/10045 20130101; B32B 17/10761 20130101; C03C 3/085
20130101 |
Class at
Publication: |
65/33.8 |
International
Class: |
C03C 10/00 20060101
C03C010/00 |
Foreign Application Data
Date |
Code |
Application Number |
Nov 13, 2008 |
DE |
10 2008 043 718.2 |
Claims
1. A process for producing a transparent plate, said process
comprising the following steps: a) preparing a green glass body
comprising glass of a Li.sub.2O--Al.sub.2O--SiO.sub.2 system; and
b) using a ceramization program, said ceramization program
comprising heating the green glass body, for the purpose of
nucleation, to a nucleation temperature of 750.+-.20.degree. C. and
holding said nucleation temperature for 20.+-.15 minutes, further
heating of the green glass body, for the purpose of ceramization,
to a ceramization temperature of 900.+-.20.degree. C. and holding
said ceramization temperature for 20.+-.15 minutes, and cooling to
room temperature; wherein said transparent plate is a lithium
aluminosilicate glass ceramic with a composition, expressed in wt.
%, comprising: TABLE-US-00006 Li.sub.2O 3.0-4.5 Al.sub.2O.sub.3
18.0-24.0 SiO.sub.2 55.0-70.0 TiO.sub.2 0.01-2.3 ZrO.sub.2 0.01-2.0
.SIGMA. TiO.sub.2 + ZrO.sub.2 0.5-4.3 SnO.sub.2 .sup. 0-0.2 MgO
.sup. 0-0.8 Fe.sub.2O.sub.3 40-200 ppm As.sub.2O.sub.3 0.3-0.9.
2. The process according to claim 1, wherein said transparent plate
has a thermal expansion coefficient (CTE) from
-0.15.times.10.sup.-6/K to +0.15.times.10.sup.-6/K at 30 to
700.degree. C.
3. The process according to claim 2, wherein said thermal expansion
coefficient (CTE) is from -0.05.times.10.sup.-6/K to
-0.10.times.10.sup.6/K at 30 to 700.degree. C.
4. The process according to claim 1, where said composition
comprises from 40 to 130 ppm of said Fe.sub.2O.sub.3.
5. The process according to claim 1, wherein said composition
further comprises, in wt. %: TABLE-US-00007 BaO 0-3.sup. Na.sub.2O
0-1.5 ZnO 0-2.5.
6. The process according to claim 1, wherein the transparent plate
has a brightness value for transmitted normal light observed at an
angle of 2.degree. of .gtoreq.80 for a plate thickness of 4 mm.
Description
CROSS-REFERENCE
[0001] This is a divisional of U.S. patent application Ser. No.
12/616,982, filed on Nov. 12, 2009, which claims priority of
invention based on German Patent Application 10 2008 043 718.2
filed on Nov. 13, 2008 in Germany. The aforesaid German Patent
Application contains subject matter described and claimed herein
below.
BACKGROUND OF THE INVENTION
[0002] The inventions described herein comprise a transparent plate
made of lithium aluminosilicate glass ceramic having a high
transmission, a process for making same and also transparent plate
laminates comprising at least one of the plates of the lithium
aluminosilicate glass ceramic according to the invention and the
use thereof as armored glass or in bullet-proof vests.
[0003] Until now, the inherent color of transparent glass ceramics
has been too strong. The reasons for the inherent color of
transparent glass ceramics can vary. The constituents of the raw
material mixtures for the melts contain the coloring element Fe as
an impurity. The use of the refining agents Sb.sub.2O.sub.3 and
CeO.sub.2 also results in a slight inherent color. The described
brownish-yellow intrinsic color of the transparent glass ceramics
is based substantially on electronic transitions occurring on
colored complexes which absorb in the region of visible light and
in which the component required for nucleation, namely the Ti ion,
takes part. The most frequent absorbing color complex stems from
the formation of adjacent Fe and Ti ions between which electronic
charge transfers take place. Sn--Ti complexes also impart an
inherent color. The Fe/Ti color complexes lead to a red-brown
discoloration and the Sn/Ti color complexes to a yellow-brown one.
The formation of these adjacent color complexes takes place already
during the cooling of the parent glass and particularly during the
subsequent ceramization of the glass ceramic. In the melt, the ions
are still uniformly distributed, but during cooling at high
temperatures and during ceramization they preferably bind to each
other. As a result, during the ceramization of the transparent
glass ceramics, the inherent color intensifies very markedly
compared to that of the parent glass. By absorption in the
short-wave region of the visible spectrum, transparent flat glasses
and particularly the glass ceramics produced therefrom assume a
pronounced inherent color which in-creases considerably with
thickness.
[0004] It is known that the inherent color of glass ceramics can be
reduced by overcoloring. The principle of overcoloring an
undesirable color tinge naturally leads to stronger light
absorption thus reducing the overall transmission, because the
absorptions taking place are neutralized by the absorptions of
complementary light portions by the overcoloring agent.
[0005] Glass ceramic plates find use in, among other applications,
bullet-proof glass plates. In the production of such glass plates,
several different glass or glass ceramic layers and plastic sheets
are linked. The temperature- and pressure-controlled process of
linking the individual layers and plastic materials to each other,
in particular, is time-consuming and cost-intensive. The many
interfacial transitions between glass plates and plastic materials
result in poor transmission characteristics which may lead to the
formation of interference fringe patterns in the form of Newton
fringes. Also, the large amount of glass, namely the high number of
glass plates in the known bullet-proof plates results in their
exhibiting a very high weight per unit area. The high weight per
unit area leads to a significant construction cost for installation
and vitrification.
SUMMARY OF THE INVENTION
[0006] Hence, one object of the present invention is to provide a
process for producing a glass ceramic plate, which is free of the
disadvantages of the prior art plates and which is suitable for use
as armored glass or in a bullet-proof .vest.
[0007] Another object of the present invention is to provide glass
ceramic plates exhibiting high overall transmission for visible
light. In particular, these glass ceramic plates show a high
overall transmission for visible light which manifests itself in a
high brightness value for transmitted standard light A under
2.degree. observation) (Y.sub.A/2.degree.).
[0008] Another object of the present invention is to provide plate
laminates, comprising at least one glass ceramic plate, exhibiting
high overall transmission for visible light and/or a high hardness.
In particular, these plate laminates show a high overall
transmission for visible light and their light brightness value Y
for transmitted standard light A under 2.degree. observation is
Y.sub.A/2.degree.>50.
[0009] Another object of the present invention is to provide plate
laminates, comprising at least one glass ceramic plate, said
laminates exhibiting better resistance to dynamic stresses compared
to plate laminates with conventional glass ceramic plates and the
same weight per unit area.
[0010] Another object of the present invention is to provide plate
laminates, comprising at least one glass ceramic plate, said
laminates exhibiting improved transparency thus ensuring bullet
impact re-sistance meeting the requirements of NATO Standardization
Agreement, STANAG 4569, Level 2 and 3. The plate laminates also
ensure bullet impact resistance against armor-piercing projectiles,
namely against armor-breaking projectiles.
[0011] The aforesaid objectives are reached by providing a
transparent plate made of lithium aluminosilicate glass ceramic
containing the following constituents in weight %, based on the
overall composition:
TABLE-US-00001 Li.sub.2O 3.0-4.5 Al.sub.2O.sub.3 18.0-24.0
SiO.sub.2 55.0-70.0 TiO.sub.2 0-2.3 ZrO.sub.2 0-2.0
.SIGMA.TiO.sub.2 + ZrO.sub.2 0.5-4.3 SnO.sub.2 0-0.2 MgO 0-0.8
Fe.sub.2O.sub.3 40-200 ppm As.sub.2O.sub.3 0.3-0.9 as chemical
refining agent.
[0012] The plate preferably contains from 40 to 130 ppm of
Fe.sub.2O.sub.3, and the TiO.sub.2 content is preferably higher
than 0.01 wt. % and particularly higher than 0.5 wt. %.
[0013] The reduction in Fe content is economically feasible only to
a certain degree. A certain amount of Fe or Fe.sub.2O.sub.3 always
enters the mixture with the industrially used raw materials for the
production of the glass and with the abraded material from the
units for the production, homogenization and transportation of the
mixture. Because of the elevated cost of high-purity raw materials
or of the special measures applied to industrial units, it is
economically no longer feasible to drop the Fe.sub.2O.sub.3 content
of industrially produced transparent glass ceramics below about 40
ppm.
[0014] For purposes of the present invention, by a glass ceramic is
meant an inorganic, nonporous material with a crystalline phase and
a glass phase in which, as a rule, the matrix, namely the
continuous phase, is a glass phase. The combination of a
crystalline and a glass phase imparts to a glass ceramic its
special properties.
[0015] For purposes of the present invention, visible light is
light with a wavelength from 380 to 780 nm.
[0016] The brightness value Y of the CIE-xyz color-measuring system
is always reported for transmitted standard light A and for an
observation angle of 2.degree. and can be determined from
wavelength-resolved transmission spectra with the aid of the
CIE-defined eye-sensitivity curves x(.lamda.), y(.lamda.) and
z(.lamda.) (tristimulus curves) (International Illumination
Commission Proceedings, 1931, Cambridge University Press,
Cambridge, or DIN 5031):
X=.intg..sub.0.sup..infin.I(.lamda.) x(.lamda.)d.lamda.
Y=.intg..sub.0.sup..infin.I(.lamda.) y(.lamda.)d.lamda.
Z=.intg..sub.0.sup..infin.I(.lamda.) z(.lamda.)d.lamda.,
wherein .lamda. is a wavelength of monochromatic light; l(.lamda.)
is an intensity of the monochromatic light, specifically
l(.lamda.)=T(.lamda.)f.sub.A/2(.lamda.), wherein T(.lamda.) is the
wavelength-resolved transmission of the sample and
f.sub.A,2(.lamda.) is the wavelength-resolved intensity factor for
standard light A observed under a 2.degree. angle.
[0017] The factor coordinates are calculated from:
x = X X + Y + Z ##EQU00001## y = Y X + Y + Z ##EQU00001.2## z = Z X
+ Y + Z . ##EQU00001.3##
[0018] The achromatic point for standard light A is defined by:
x.sub.u,A=0.4476
y.sub.u,A=0.4074.
[0019] The abbreviation CTE refers to the linear thermal expansion
coefficient of a material that can be indicated for different
temperature ranges. CTE (.DELTA.l/l.sub.o.DELTA.T) in ppm/K is
determined by dilatometric measurements with a TDA (thermal
dilatometric analyzer), Harrop Model TD 710, in accordance with DIN
ISO 7991.
[0020] Preferably, the transparent plate contains the following
additional constituents, in wt. % based on the overall
composition:
TABLE-US-00002 BaO 0-3.sup. Na.sub.2O 0-1.5 ZnO 0-2.5 ZrO.sub.2
0.5-2.
[0021] The oxides Li.sub.2O, Al.sub.2O.sub.3 and SiO.sub.2 are
required constituents of the glass ceramic and are present within
the preferred limits cited in the claims. In general, a minimum
amount of 3 wt. % of Li.sub.2O is needed, but Li.sub.2O contents
exceeding 4.5 wt. % often cause undesirable devitrification during
the manufacturing process. An Li.sub.2O content of 3.2 to 4.3 wt. %
gives particularly good results.
[0022] To prevent excessively high glass viscosities and to
suppress the tendency toward undesirable devitrification during
shaping, the Al.sub.2O.sub.3 content is limited to a preferred
minimum of 18 wt. % to a preferred maximum of 24 wt. %. When the
Al.sub.2O.sub.3 content is below 19 wt. %, the transparency of the
glass ceramic is reduced. The SiO.sub.2 content should preferably
amount to a maximum of 70 wt, %, particularly 68 wt. %, because
this component causes a marked increase in the viscosity of the
glass. Hence, higher SiO.sub.2 contents are deleterious for the
melting of the glasses because of the temperature stress exerted
during shaping. The minimum SiO.sub.2 content should preferably
amount to 55 wt. % and particularly 60 wt. %.
[0023] MgO and ZnO can be incorporated into the crystalline phase
as additional components. Because of the problem of undesirable
formation of crystal phases such as Zn spinel during ceramization,
the ZnO content is limited to a maximum of 2.5 wt. % and preferably
to a maximum of 2 wt. %. The MgO content is limited to a maximum of
0.8 wt. % and preferably to a maximum of 0.65 wt. %, because
otherwise the expansion coefficient of the glass ceramic is
increased inadmissibly. A low MgO content is also advantageous in
suppressing the inherent color of the glass ceramic. As a rule, a
minimum MgO content of 0.3 wt. % is required to prevent the thermal
expansion of the glass ceramic in the temperature range from
30.degree. C. to 700.degree. C. from decreasing to negative values
below-0.3.times.10.sup.-6/K.
[0024] The glass ceramic contains as nucleating agents TiO.sub.2
and ZrO.sub.2 and preferably only TiO.sub.2. SnO.sub.2 can also
serve as nucleating agent. The amount of TiO.sub.2 used is
preferably in the range between 1.8 and 2.3 wt. % and most
preferably between 2.0 and 2.3 wt. %. The amount of ZrO.sub.2 is
preferably in the range between 0.5 and 2 wt. % and most preferably
between 1.5 and 2 wt. %. If these two nucleating agents are used
together, the sum of the amounts of TiO.sub.2+ZrO.sub.2 should not
exceed 4.3 wt. %, and preferably not 2.3 wt. %.
[0025] The aforesaid amounts of nucleating agents allow
ceramization to be carried out in a short time, preferably within a
period of 1 to 2 hours. Because of the low amount of TiO.sub.2, the
strength of the inherent color is also reduced.
[0026] ZnO, MgO and BaO, are added to the composition to improve
the melt properties of the glass ceramic and to stabilize the glass
phase. ZnO also makes it possible to influence the thermal
expansion coefficient (CTE) while MgO and BaO cause this
coefficient to increase. Also, higher contents of the aforesaid
metals can affect the crystallization behavior during the
conversion of the glass into the glass ceramic and they exert a
deleterious effect on the thermal stress resistance of the glass
ceramic. Preferably, the glass ceramic of the present invention
contains 1 to 2.6 wt. % of ZnO, 0.3 to 0.8 wt. % of MgO and 0 to 3
wt. % of BaO. Most preferably, the glass ceramic of the present
invention contains 1 to 2 ZnO, 0.3 to 0.65 MgO and 0 to 2 BaO, each
expressed in wt. %.
[0027] The glass ceramic of the present invention can also contain
0 to 1.5 wt. % and preferably 0 to 1 wt. % of Na.sub.2O. After
ceramization, the alkali metal ions, for example the sodium ions,
remain in the residual glass phase. They increase the thermal
expansion coefficient and can therefore be used when the thermal
expansion coefficient values are too negative. If, however, they
are used in excessive amounts, the thermal expansion becomes too
high, and the nucleation is difficult to control.
[0028] The glass ceramics according to the invention are refined by
use of arsenic oxide, the refining agent commonly used in the
Li.sub.2O--Al.sub.2O.sub.3--SiO.sub.2 system. Alternatively or in
combination, SnO.sub.2 can also be used in amounts of up to 0.2 wt.
%, especially for high-temperature refining at >1700.degree. C.
Other refining agents, for example, Sb.sub.2O.sub.3, CeO.sub.2,
sulfate compounds, chloride compounds or fluoride compounds, can
also be added to the glass melt. The total amount of refining
agents and additives should not exceed 1.2 wt. %. Preferably,
As.sub.2O.sub.3 is used as the only refining agent.
[0029] At low contents of As.sub.2O.sub.3, Sb.sub.2O.sub.3 or
SnO.sub.2 refining agents, it may be necessary to combine the
chemical refining with high-temperature refining above 1700.degree.
C. if good bubble quality with bubble numbers below 5 bubbles/kg of
glass (based on bubble sizes >0.1 mm) is desired. It is
particularly advantageous, if inherent color is to be avoided, to
refine the glass ceramic exclusively with As.sub.2O.sub.3 as the
refining agent and not to use antimony oxide and tin oxide as
refining agents. Other refining agents, such as sulfate, chloride
or fluoride compounds, may also be added in a total amount of up to
1 wt. %.
[0030] Preferably, the thickness of the transparent glass ceramic
plate is in the range from 2 and 20 mm, particularly in the range
from 4 and 15 mm and especially in the range from 6 and 12 mm.
[0031] The transparent plate according to the invention, at a
thickness of 4 mm, preferably shows a brightness value
Y.sub.A/2.degree. of >80, preferably >85 and most preferably
>89.
[0032] The thermal expansion coefficient (GTE) between 30 and
700.degree. C. is preferably in the range between -0.15 to
+0.15.times.10.sup.-6/K and more preferably in the range between
-0.05 to 0.1.times.10.sup.-6/K.
[0033] The Knoop hardness of a glass ceramic according to the
invention is determined in accordance with DIN ISO 9385, edition of
1991-01.
[0034] The Knoop diamond is impressed under a load of 0.1 N for 20
seconds. The Knoop hardness of the glass ceramic plate of the
invention is HK.sub.01/.sub.20.gtoreq.500, preferably
HK.sub.01/.sub.20.ltoreq.550 and most preferably
HK.sub.0.1/20.gtoreq.580.
[0035] Another object of the invention is a process for producing
the glass ceramic of the invention.
[0036] It is generally known that glasses of the
Li.sub.2O--Al.sub.2O.sub.3--SiO.sub.2 system can be converted into
glass ceramics in which high-quartz mixed crystals are the main
crystal phase. To this end, the following procedure is used: A
suitable composition of suitable raw materials is melted, refined,
homogenized and then, while hot, shaped to form a glass blank or
green body, for example by rolling, casting, pressing or, recently,
floating. By "green body" of a glass ceramic is meant a glassy body
obtained from a melt of suitable composition which by treatment
according to a suitable temperature program can be converted into a
glass ceramic.
[0037] The cooling and annealing of the molten green body is
followed by a heat treatment whereby the glass is converted into a
glass ceramic by controlled bulk crystallization. In the course of
this heat treatment, in a first conversion step ("nucleation agent
separation") crystallization nuclei of the same or different kind
are formed in the glass. By crystallization nuclei or crystal
nuclei are meant submicroscopic crystalline aggregates of a
characteristic size. In a second conversion step
("crystallization"), possibly at a slightly higher temperature,
crystals or crystallites grow on the crystal nuclei. The glass
ceramic of the invention is preferably produced in accordance with
the following ceramization program: [0038] heating to a temperature
of 750.+-.20.degree. C. and holding this temperature for 20.+-.15
minutes; [0039] further heating, for purposes of ceramization, to a
temperature of 900.+-.20.degree. C. and holding this temperature
for 20.+-.15 minutes, then cooling to room temperature.
[0040] The cooling to room temperature requires no particular
temperature program. As a rule, it is carried out by exposing the
hot plates to room air. The cooling time usually ranges from -10
K/min to <-100 K/min.
[0041] Another object of the present invention is a transparent
plate of lithium aluminosilicate glass ceramic which contains the
following constituents, expressed in wt. % based on the total
composition:
TABLE-US-00003 Li.sub.2O 3.0-4.5 Al.sub.2O.sub.3 18.0-24.0
SiO.sub.2 55.0-70.0 TiO.sub.2 0-2.3 ZrO.sub.2 0-2.0
.SIGMA.TiO.sub.2 + ZrO.sub.2 0.5-4.3 SnO.sub.2 0-0.2 MgO 0-0.8
Fe.sub.2O.sub.3 40-200 ppm As.sub.2O.sub.3 0.3-0.9 as chemical
refining agent,
and is prepared in accordance with the following ceramization
program: [0042] heating for the purpose of nucleation to a
temperature of 750.+-.20.degree. C. and holding this temperature
for 20.+-.15 minutes; [0043] further heating for the purpose of
ceramization to a temperature of 900.+-.20.degree. C. and holding
this temperature for 20.+-.15 minutes, then cooling to room
temperature.
[0044] The aforesaid transparent glass ceramic plate is appropriate
for the production of plate laminates with a high bullet
penetration resistance and high transparency for visible and
infrared light in the wavelength range between 380 and 1100 nm.
Moreover, the thermo-mechanical properties of the glass ceramic
according to the invention make it possible to use it in fire
safety glazing, as fireplace sight glass, ceramic hob, substrate
for semiconductor materials or substrate for magnetic storage
plates.
[0045] Another object of the present invention is a transparent
plate laminate which, in particular, shows a high resistance to
bullet penetration and a high optical transmission.
[0046] The plate laminate according to the invention comprises at
least one transparent glass ceramic plate (a), as described in the
foregoing, optionally at least one plate (b) selected from the
group consisting of borosilicate glass, soda lime glass and
aluminosilicate glass which can also be chemically or thermally
prestressed, and at least one plate (c) selected from the group
consisting of polycarbonate, polyacrylate, particularly poly(methyl
methacrylate), cellulose acetate butyrate, nylon, polyolefin,
polyester, polyurethane and a mixture thereof.
[0047] According to German industrial standard DIN 52290, part 3
(06/1984), and/or according to German industrial standard DIN
52290, part 2 (11/1988), the plate laminate of the invention exerts
breakthrough-inhibiting properties. The plate laminate according to
the invention also ensures bullet penetration resistance that meets
the requirements of the NATO Standardization Agreement, STANAG
4569, Levels 2 and 3.
[0048] Preferably, plate (c) consists of transparent polycarbonate
(PC), poly(methyl methacrylate) (PMMA) or polyurethane (PU).
[0049] The number of plates in the transparent plate laminate is
limited only by the requirements for high transmission it must
meet. The number of plates (a), (b) and (c) preferably amounts to 2
to 10, more preferably to 3 to 9 and most preferably to 4 to 8. A
plate (a) is preferably oriented outward or is furthest away from
the object to be protected. For armored glass, for example, this
means that plate (a) is the first plate that must withstand
external influences. Preferably, plate (c) is oriented closest to
the object to be protected. In the case of armored glass, this
means that plate (c) is the plate that lines the internal space of
a motor vehicle.
[0050] Preferred is a plate arrangement that shows the following
plate sequence, in all cases from the outside (furthest away from
the object to be protected) toward the inside (closest to the
object to be protected):
8-Plate Laminate Embodiments
[0051] (a)-(a)-(a)-(a)-(a)-(a)-(a)-(c)
(b)-(b)-(a)-(a)-(b)-(b)-(a)-(c) (a)-(a)-(a)-(b)-(b)-(b)-(b)-(c)
(a)-(a)-(b)-(b)-(a)-(a)-(a)-(c) (a)-(a)-(b)-(b)-(a)-(a)-(b)-(c)
7-Plate Laminate Embodiments
[0052] (a)-(a)-(a)-(b)-(b)-(b)-(c) (b)-(b)-(b)-(a)-(a)-(b)-(c)
(a)-(a)-(b)-(a)-(b)-(b)-(c)
6-Plate Laminate Embodiments
[0053] (a)-(a)-(b)-(b)-(a)-(c) (a)-(a)-(a)-(b)-(b)-(c)
(a)-(b)-(a)-(b)-(b)-(c)
[0054] Plate (b) preferably has a thickness ranging from 3 to 20
mm, particularly from 5 to 15 mm and most preferably from 5 to 10
mm.
[0055] The thickness of plate (c) is preferably in the range from 3
to 15 mm, particularly from 5 to 15 mm and most preferably from 8
to 13 mm. The thickness of plate (a) in the plate laminate is
preferably in the range from 3 to 20 mm, particularly in the range
from 4 to 15 mm and most preferably in the range from 6 to 12
mm.
[0056] The thickness of the plate laminate is preferably in the
range from 30 to 100 mm, particularly in the range from 40 to 80 mm
and most preferably in the range from 60 to 80 mm.
[0057] Preferably, plates (a)-(a), (a)-(b) and (b)-(b),
independently of each other, are attached to each other with a
bonding agent selected from the group consisting of casting resins
or reactive resins based on polyurethanes, polyvinylbutyral (PVB),
cross-linked polyurethanes, partly cross-linked polyurethanes,
polyureas, epoxides, unsaturated or saturated polyesters,
polybutylene terephthalates (PBT), poly-(meth)acrylates, silicones
or silicone resin polymers, or from the group of hot-melt
adhesives, coatings or sealants selected from the group consisting
of hot-melt adhesives based on polyethylene or copolymers thereof,
particularly ethylene vinylacetate (EVA) or polyvinyl acetate or
mixtures thereof. More preferably plates (a)-(a), (a)-(b) and
(b)-(b), independently of each other, are connected to each other
with a bonding agent selected from the group consisting of casting
resins or reactive resins based on polyurethanes, polyvinylbutyral
and hot-melt adhesives based on ethylene vinylacetate. Most
preferably, plates (a)-(a), (a)-(b) and (b)-(b) are connected with
polyvinylbutyral or polyurethane in the form of a film.
[0058] Plates (a)-(c), (b)-(c) and (c)-(c), independently of each
other, are attached to each other with a bonding agent selected
from the group consisting of casting resins or reactive resins
based on poly-urethanes, polyvinylbutyral (PVB), cross-linked
polyurethanes, partly cross-linked polyurethanes, polyureas,
epoxides, unsaturated or saturated polyesters, polyethylene
terephthalates (PET), poly-butylene terephthalates (PBT),
poly(meth)acrylates, silicones and silicone resin polymers, or from
the group of hot-melt adhesives, coatings or sealants selected from
the group consisting of hot-melt adhesives based on polyethylene or
copolymers thereof, particularly ethylene vinyl acetate (EVA), or
polyvinyl acetate or mixture thereof. Most preferably, the (a)-(c),
(b)-(c) and (c)-(c) plates, independently of each other, are
connected by means of a bonding agent selected from the group
consisting of casting resins or reactive resins based on
polyurethanes, polyvinylbutyral and hot-melt adhesives based on
ethylene vinylacetate. Most preferably, the (a)-(c), (b)-(c) and
(c)-(c) plates are connected by means of polyvinylbutyral in the
form of a film.
[0059] A transparent plate laminate according to the present
invention that uses the transparent glass ceramic plates of the
invention shows a lower weight per unit area than do corresponding
transparent plate laminates containing conventional glasses or
glass ceramics. Preferably, the weight per unit area of the plate
laminate is in the range between 50 and 150 kg/m.sup.2, more
preferably in the range between 50 and 120 kg/m.sup.2 and most
preferably in the range between 50 and 100 kg/m.sup.2 and it meets
the requirement of "NATO AEP-55 STANAG 4569--Level II or III" by
stopping, for example, hard-core bullets of the 7.62.times.39 API
BZ type striking at 695 m/s, and bullets with a tungsten carbide
core of the 7.62.times.51 AP type striking at 930 m/s or hard-core
bullets of the 7.62.times.54R B32 API type striking at 854 m/s.
[0060] The thickness of the bonding agent layers preferably ranges
from 0.05 to 2 mm, more preferably from 0.1 to 1 mm and most
preferably from 0.2 to 0.8 mm.
[0061] Another object of the present invention is a process for
producing the plate laminate that comprises the following steps:
[0062] cutting out plates (a), (b) and (c), [0063] cleaning plates
(a), (b) and (c), [0064] stacking up the plates and introducing a
bonding agent into the spaces between the individual plates (a),
(b) and (c), possibly exposing the stack to heat treatment to
activate the bonding agent, possibly under vacuum or by exerting
high pressure on the stack, and [0065] cooling the laminate.
[0066] A similar process for producing a laminate is described, for
example, in US 2008-187721 AA (SO-CLIMA GmbH) or EP 0 331 648.
[0067] By the invention-provided possibility to use only few and
possibly thin glass ceramic plates, the transmission properties of
the plate laminate of the invention are much improved. Also, the
plate laminates according to the invention possess outstanding
color neutrality because of the use of glass ceramic plates which
can be thinner compared to those of the prior art.
[0068] Another object of the present invention is the use of a
glass ceramic plate according to the invention or the use of a
plate laminate according to the invention, as described in the
foregoing, as part of an armored glass or as part of a bullet-proof
vest.
[0069] The armored glass according to the invention ensures maximum
energy absorption when a bullet strikes. This splinter-proof design
preferably serves to protect the persons present in a motor vehicle
or building provided with such an armored glass from being hit by
flying glass splinters stemming from a glass pane hit by a
bullet.
BRIEF DESCRIPTION OF THE DRAWING
[0070] FIG. 1 is a schematic perspective view of a plate laminate
of the present invention.
DESCRIPTION OF THE PREFERRED EMBODIMENTS
[0071] G1 to G8 represent plates made of glass, glass ceramic or
plastic material.
[0072] K1 to K7 represent layers of bonding agents based on a
plastic material, particularly films of polyvinylbutyral or
polyurethane that as a rule are currently used for the production
of laminated glass.
EXAMPLES
[0073] Four different glass ceramics of different composition,
examples 1 to 4 in Table 1 here below, were prepared (data are
given in wt. % based on oxides). The brightness value
Y.sub.A,.sub.2.degree. Is GIVEN for a glass thickness of 4 mm and
the linear thermal expansion coefficient (CTE) is given for the
range between 30 and 700.degree. C. The linear thermal expansion
coefficient CTE was determined in the 30 to 700.degree. C.
temperature range in accordance with DIN ISO 7991 by use of a
Thermal Dilatometric Analyzer, Harrop Model TD 710.
[0074] To prepare the glass ceramics, first a green glass of the
same composition was prepared in the usual manner. From this green
glass, glass plates of the desired thickness were then made. The
glass plates were then ceramized in the known manner to form glass
ceramic plates, the nucleating agents having been formed in the
glass at a temperature of 750.degree. C. and a residence time of 20
minutes. The glass was then heated to the crystallization
temperature of 830.degree. C. The crystallization was allowed to
occur at a temperature ranging from 830.degree. C. to 900.degree.
C., the temperature being raised from 830.degree. C. to 900.degree.
C. at a rate of 10 K per minute with a 10-minute residence time at
900.degree. C.
[0075] To determine the brightness value Y.sub.A/2.degree., first
the wavelength-dependent transmission T(.lamda.) of a 4-mm-thick
sample of the glass ceramic was measured and standardized to normal
light A
l(.lamda.)=T(.lamda.)f.sub.A(.lamda.)(A=350 . . . 800 nm)
[0076] Then Y was then calculated with the aid of the CIE-defined
eye sensitivity curves y.sub.avg(.lamda.) (International
Illumination Commission Proceedings, 1931, Cambridge University
Press, Cambridge, or DIN 5031):
Y=.intg..sub..lamda.=380 nm.sup..lamda.=800 nmI(.lamda.)
y(.lamda.)d.lamda.
TABLE-US-00004 TABLE 1 GLASS CERAMIC COMPOSITIONS, BRIGHTNESS
VALUES AND THERMAL EXPANSION COEFFICIENTS THEREOF Example: 1 2 3 4
Al.sub.2O.sub.3 21.96 21.70 21.50 21.67 As.sub.2O.sub.3 0.35 0.31
0.31 0.85 BaO 2.00 1.99 1.94 1.97 Fe.sub.2O.sub.3 0.0050 0.0110
0.0120 0.0130 Li.sub.2O 3.78 3.76 3.66 3.72 MgO 0.60 0.58 0.58 0.58
Na.sub.2O 0.55 0.53 0.52 0.52 SiO.sub.2 65.04 65.50 65.80 64.96
TiO.sub.2 2.27 2.11 2.29 2.29 ZnO 1.70 1.68 1.64 1.67 ZrO.sub.2
1.73 1.80 1.76 1.77 SnO.sub.2 <0.01 <0.01 <0.01 <0.01
Y(A/2.degree.); 4 mm 89.7 89.5 89.3 89.7 CTE* (30-700.degree. C.)
-0.08 -0.11 -0.1 -0.1 *CTE values are in units of 10.sup.-6/K.
[0077] The glass ceramic of the invention according to example 4
was incorporated into a plate laminate. The plate laminate was
prepared in an autoclave by common lamination methods using
different glass and glass ceramic plates by interposing in each
case one PVB film in accordance with the process parameters
recommended by the manufacturer of the PVB film (BUTACITE.RTM.
Clear, manufactured by DuPont).
[0078] Eleven plate laminates of different structures are listed in
Table 2.
TABLE-US-00005 TABLE 2 TRANSPARENT PLATE LAMINATE COMPOSITION AND
PROPERTIES Ex. G1 K1 G2 K2 G3 K3 G4 K4 G5 K5 G6 K6 G7 K7 G8 6b 2-4
mm 7 2-10 mm 7 2-10 mm 7 2-10 mm 7 2-10 mm 7 2-10 mm 7 2-10 mm 7
6-12 mm 6a 2-4 mm 7 2-10 mm 7 1-8 mm 7 1-8 mm 7 2-10 mm 7 1-8 mm 7
1-8 mm 7 6-12 mm 6 2-4 mm 7 1-8 mm 7 1-8 mm 7 1-8 mm 7 1-8 mm 7 1-8
mm 7 1-8 mm 7 6-12 mm 5 1-3 mm 7 1-8 mm 7 1-8 mm 7 1-8 mm 7 1-8 mm
7 1-8 mm 7 1-8 mm 7 6-12 mm 4a 1-3 mm 7 1-8 mm 7 1-8 mm 7 2-10 mm 7
2-10 mm 7 2-10 mm 7 6-12 mm 4 1-3 mm 7 1-8 mm 7 1-8 mm 7 1-8 mm 7
1-8 mm 7 1-8 mm 7 6-12 mm 3a 1-3 mm 7 1-8 mm 7 1-8 mm 7 2-10 mm 7
2-10 mm 7 6-12 mm 3 1-3 mm 7 1-8 mm 7 1-8 mm 7 1-8 mm 7 1-8 mm 7
6-12 mm 2a 1-3 mm 7 1-8 mm 7 1-8 mm 7 2-10 mm 7 6-12 mm 2 1-3 mm 7
1-8 mm 7 2-10 mm 7 1-8 mm 7 6-12 mm 1 5-8 mm 7 5-8 mm 7 5-8 mm 7
5-8 mm 7 6-12 mm Thickness, wt./unit Antiballistic Example mm area,
kg/m.sup.2 Y(A/2.degree.) limit 6b 78.66 158 52.35 820 6a 70.66
151.5 51.2 830 6 66.66 144 50.72 850 5 65.66 147 49.84 860 4a 63.28
131 53.9 760 4 57.28 126 53.11 780 3a 52.9 109 57.17 620 3 48.9
105.5 56.6 630 2a 44.52 88 60.96 520 2 40.52 85 60.33 520 1 45.52
97.5 49.4 600
[0079] In Table 2, G1 to G8 indicate the bullet-proof layers and K1
to K7 the layers of the lamination film. The constituents of the
individual layers are numbered, and when necessary their thickness
is indicated in mm. The numbering of the individual layers has the
following meaning: [0080] 1: Glass ceramic of the invention as per
Example 4, Table 1. [0081] 2: Floated borosilicate glass with an
expansion coefficient CTE.sub.30 . . . .sub.300 of
3.3.times.10.sup.-6 K.sup.-1 (BOROFLOAT.RTM. 33, Schott AG,
composition in wt. % about 81 SiO.sub.2, 13 B.sub.2O.sub.3, 4
Na.sub.2O+K.sub.2O, 2 Al.sub.2O.sub.3). [0082] 5: Prior-art glass
ceramic (EP 1,837,312, Example 3, rounded off composition in wt. %:
65.3 SiO.sub.2, 21.8 Al.sub.2O.sub.3, 3.7 Li.sub.2O, 2.3 TiO.sub.2,
2 BaO, 1.7 ZnO, 1.8 ZrO.sub.2, 0.6 MgO, 0.5 Na.sub.2O, 0.3
As.sub.2O.sub.3, 0.1 Nd.sub.2O.sub.3). [0083] 6: Commercial
impact-resistant poly(methyl methacrylate) (PLEXIGLAS RESIST.RTM.,
Evonic industries, U.S. Pat. No. 5,726,245 A). [0084] 7:
Polyvinylbutyrate film, thickness 0.38 mm (BUTACITE.RTM. Clear,
DuPont).
[0085] To determine the weight per unit area, kg.times.m.sup.-2, a
50.times.50 cm.sup.2 plate was weighed and the result was converted
into 1.times.m.sup.2. The antiballistic limit m s.sup.-1 was
determined with a 7.62-mm caliber bullet weighing 10 g and
containing steel core. Different bullet speeds were produced by
means of different propelling charges. To determine the
antiballistic limit, the test laminates were shot at with
projectiles of different speed, and the antiballistic limit was
then determined on the basis of the impact pattern for the
different speeds.
[0086] Table 2 clearly indicates that plate laminates of the glass
ceramic of the invention show a lower weight per unit area than do
plate laminates of a different composition but with a comparable
ballistic limit.
[0087] While the invention has been illustrated and described as
embodied in a process for producing a highly transparent impact
resistant glass ceramic, it is not intended to be limited to the
details shown, since various modifications and changes may be made
without departing in any way from the spirit of the present
invention.
[0088] Without further analysis, the foregoing will so fully reveal
the gist of the present invention that others can, by applying
current knowledge, readily adapt it for various applications
without omitting features that, from the standpoint of prior art,
fairly constitute essential characteristics of the generic or
specific aspects of this invention.
[0089] What is claimed is new and is set forth in the following
appended claims.
* * * * *