OPTICAL FILTER GLASS CERAMIC AND OPTICAL FILTER

Abstract

A glass ceramic for an optical filter and an optical filter are obtained that have both thermal expansion characteristics for preventing refractive index fluctuations at a usage temperature of a filter member and mechanical characteristics considering durability, and further have excellent workability.

An internal transmittance of the glass ceramic for an optical filter is 0.970 or more with respect to light having a wavelength of 1550 nm when a thickness of the glass ceramic is 1 mm. The glass ceramic includes, by mass % in terms of oxide, 40.0% to 70.0% of a SiO.sub.2 component, 11.0% to 25.0% of an Al.sub.2O.sub.3 component, 5.0% to 19.0% of a Na.sub.2O component, 0% to 9.0% of a K.sub.2O component, 1.0% to 18.0% of one or more components selected from a MgO component and a ZnO component, 0% to 3.0% of a CaO component, and 0.5% to 12.0% of a TiO.sub.2 component.

Claims

1. A glass ceramic for an optical filter, an internal transmittance of the glass ceramic being 0.970 or more with respect to light having a wavelength of 1550 nm when a thickness of the glass ceramic is 1 mm; the glass ceramic comprising, by mass % in terms of oxide: 40.0% to 70.0% of a SiO.sub.2 component; 11.0% to 25.0% of an Al.sub.2O.sub.3 component; 5.0% to 19.0% of a Na.sub.2O component; 0% to 9.0% of a K.sub.2O component; 1.0% to 18.0% of one or more components selected from a MgO component and a ZnO component; 0% to 3.0% of a CaO component; and 0.5% to 12.0% of a TiO.sub.2 component.

2. The glass ceramic for an optical filter according to claim 1, wherein a thermal expansion coefficient at −30° C. to +70° C. is 70×10.sup.−7/° C. to 95×10.sup.−7/° C.

3. The glass ceramic for an optical filter according to claim 1, wherein a Young's modulus is 78 GPa or more.

4. The glass ceramic for an optical filter according to claim 1, comprising, as a main crystal phase, one or more components selected from MgAl.sub.2O.sub.4, MgTi.sub.2O.sub.4, MgTi.sub.2O.sub.5, Mg.sub.2TiO.sub.4, Mg.sub.2, SiO.sub.4, MgAl.sub.2Si.sub.2O.sub.8, Mg.sub.2Al.sub.4Si.sub.5O.sub.18, Mg.sub.2TiO.sub.5, MgSiO.sub.3, NaAlSiO.sub.4, FeAl.sub.2O.sub.4, and solid solutions of these.

5. An optical filter obtained by forming a dielectric film on the glass ceramic according to claim 1.

6. A bandpass filter obtained by forming a dielectric film on the glass ceramic according to claim 1.

7. The glass ceramic for an optical filter according to claim 2, wherein a Young's modulus is 78 GPa or more.

8. The glass ceramic for an optical filter according to claim 2, comprising, as a main crystal phase, one or more components selected from MgAl.sub.2O.sub.4, MgTi.sub.2O.sub.4, MgTi.sub.2O.sub.5, Mg.sub.2TiO.sub.4, Mg.sub.2SiO.sub.4, MgAl.sub.2Si.sub.2O.sub.8, Mg.sub.2Al.sub.4Si.sub.5O.sub.18, Mg.sub.2TiO.sub.5, MgSiO.sub.3, NaAlSiO.sub.4, FeAl.sub.2O.sub.4, and solid solutions of these.

9. The glass ceramic for an optical filter according to claim 3, comprising, as a main crystal phase, one or more components selected from MgAl.sub.2O.sub.4, MgTi.sub.2O.sub.4, MgTi.sub.2O.sub.5, Mg.sub.2TiO.sub.4, Mg.sub.2SiO.sub.4, MgAl.sub.2Si.sub.2O.sub.8, Mg.sub.2Al.sub.4Si.sub.5O.sub.18, Mg.sub.2TiO.sub.5, MgSiO.sub.3, NaAlSiO.sub.4, FeAl.sub.2O.sub.4, and solid solutions of these.

10. An optical filter obtained by forming a dielectric film on the glass ceramic according to claim 2.

11. An optical filter obtained by forming a dielectric film on the glass ceramic according to claim 3.

12. An optical filter obtained by forming a dielectric film on the glass ceramic according to claim 4.

13. A bandpass filter obtained by forming a dielectric film on the glass ceramic according to claim 2.

14. A bandpass filter obtained by forming a dielectric film on the glass ceramic according to claim 3.

15. A bandpass filter obtained by forming a dielectric film on the glass ceramic according to claim 4.

Description

DETAILED DESCRIPTION OF THE EXEMPLARY EMBODIMENTS

[0026] The present disclosure is more particularly described in the following examples that are intended as illustrative only since numerous modifications and variations therein will be apparent to those skilled in the art.

[0027] As used herein, the contents of all components are expressed by mass % in terms of oxide unless otherwise specified. Here, “in terms of oxide” indicates that, when assuming that all the components constituting the glass ceramic are dissolved and converted into oxides and a total mass of the oxides is 100 mass %, an amount of oxides in each of the components contained in the glass ceramic is expressed by mass %. As used herein, “A % to B %” represents A % or more and B % or less. Further, “0%” in “0% to C %” refers to a content of 0%.

[0028] The glass ceramic according to the present disclosure contains the following components in mass % in terms of oxide:

40.0% to 70.0% of a SiO.sub.2 component,
11.0% to 25.0% of an Al.sub.2O.sub.3 component,
5.0% to 19.0% of a Na.sub.2O component,
0% to 9.0% of a K.sub.2O component,
1.0% to 18.0% of one or more components selected from a MgO component and a ZnO component,
0% to 3.0% of a CaO component, and
0.5% to 12.0% of a TiO.sub.2 component.

[0029] The SiO.sub.2 component is a glass-forming component forming a network structure of glass. The SiO.sub.2 component is preferably contained in an amount of 45.0% to 65.0%, and more preferably 50.0% to 60.0%.

[0030] The Al.sub.2O.sub.3 component is a component suitable for improving the mechanical strength. The Al.sub.2O.sub.3 component is preferably contained in an amount of 13.0% to 23.0%.

[0031] The Na.sub.2O component and the K.sub.2O component are components involved in ion exchange during chemical strengthening. The Na.sub.2O component is preferably contained in an amount of 8.0% to 16.0%. The Na.sub.2O component may be contained in an amount of 9.0% or more or 10.5% or more. The K.sub.2O component is preferably contained in an amount of 0.1% to 7.0%, and more preferably 1.0% to 5.0%.

[0032] The MgO component and the ZnO component are components contributing to mechanical strength. The ZnO component is a component effective in reducing the viscosity of glass. The one or more components selected from the MgO component and the ZnO component are preferably contained in an amount of 2.0% to 15.0%, more preferably 3.0% to 13.0%, and even more preferably 5.0% to 11.0%. The one or more components selected from the MgO component and the ZnO component may be the MgO component alone, the ZnO component alone, or both of the components, but preferably the MgO component alone.

[0033] The CaO component is a component contributing to the stabilization of glass. The CaO component is preferably contained in an amount of 0.01% to 3.0%, and more preferably 0.1% to 2.0%.

[0034] The TiO.sub.2 component is a component that may serve as a nucleating agent for crystallization. The TiO.sub.2 component is preferably contained in an amount of 1.0% to 10.0%, and more preferably 2.0% to 8.0%.

[0035] The glass ceramic may contain, as a clarifying agent, one or more components selected from an Sb.sub.2O.sub.3 component, a SnO.sub.2 component, and a CeO.sub.2 component in an amount of 0.01% to 3.0% (preferably 0.03% to 2.0%, and more preferably 0.05% to 1.0%).

[0036] The above-mentioned blending amounts may be appropriately combined.

[0037] The one or more components selected from the SiO.sub.2 component, the Al.sub.2O.sub.3 component, the Na.sub.2O component, the MgO component, and the ZnO component; and the TiO.sub.2 component may combinedly be contained in an amount of 90% or more, preferably 95% or more, even more preferably 98% or more, and still more preferably 98.5% or more.

[0038] The one or more components selected from the SiO.sub.2 component, the Al.sub.2O.sub.3 component, the Na.sub.2O component, the K.sub.2O component, the MgO component, and the ZnO component; the CaO component; the TiO.sub.2 component; and the one or more components selected from the Sb.sub.2O.sub.3 component, the SnO.sub.2 component, and the CeO.sub.2 component may combinedly be contained in an amount of 90% or more, preferably 95% or more, more preferably 98% or more, and still more preferably 99% or more. These components may also account for 100% of the glass ceramic.

[0039] The glass ceramic may or may not contain a ZrO.sub.2 component, as long as the effect of the present disclosure is not impaired. The blending amount may be 0% to 5.0%, 0% to 3.0%, or 0% to 2.0%.

[0040] As long as the effect of the present disclosure is not impaired, the glass ceramic may or may not contain a B.sub.2O.sub.3 component, a P.sub.2O.sub.5 component, a BaO component, a FeO component, a Li.sub.2O component, a SrO component, a La.sub.2O.sub.3 component, a Y.sub.2O.sub.3 component, a Nb.sub.2O.sub.5 component, a Ta.sub.2O.sub.5 component, a WO.sub.3 component, a TeO.sub.2 component, and a Bi.sub.2O.sub.3 component. The blending amount of each of the components may be 0% to 2.0%, 0% or more and less than 2.0%, or 0% to 1.0%.

[0041] Other components not described above may be added to the glass ceramic according to the present disclosure as necessary, as long as the characteristics of the glass ceramic according to the present disclosure are not impaired. For example, the glass ceramic according to the present disclosure may be colorless and transparent, but the glass may be colored, as long as the characteristics of the glass ceramic are not impaired.

[0042] There is a tendency to refrain from using components of Pb, Th, Tl, Os, Be, and Se, which are considered in recent years to be harmful chemical substances, and therefore, it is preferable that the glass ceramic substantially does not contain these components.

[0043] The glass ceramic according to the present disclosure contains, as a main crystal phase, one or more components selected from ZnAl.sub.2O.sub.4, Zn.sub.2Ti.sub.3O.sub.8, Zn.sub.2SiO.sub.4, ZnTiO.sub.3, Mg.sub.2SiO.sub.4, Mg.sub.2Al.sub.4Si.sub.5O.sub.18, NaAlSiO.sub.4, Na.sub.2Zn.sub.3SiO.sub.4, Na.sub.4Al.sub.2Si.sub.2O.sub.9, LaTiO.sub.3, and solid solutions thereof, for example.

[0044] The “main crystal phase” as used herein corresponds to a crystalline phase contained in the largest amount in the glass ceramic, which is determined from the peak of the X-ray analysis diagram.

[0045] When a glass ceramic is used for an optical filter, if the light transmittance is low, it is naturally difficult to extract a signal (decrease in S/N ratio), and thus, the light transmittance is preferably large and needs to be at least 60% or more. The glass ceramic according to the present disclosure has an internal transmittance of 0.970 or more with respect to light having a wavelength of 1550 nm in a sample thickness of 1 mm. The internal transmittance is preferably 0.980 or more, more preferably 0.985 or more, still more preferably 0.990 or more, and particularly preferably 0.995 or more. The upper limit of the internal transmittance is normally less than 1.000, for example, 0.999 or less. The light transmittance can be measured by the methods described in the Examples.

[0046] As described above, a glass ceramic for an optical filter is required to have temperature stability at the center wavelength of the band, and it is preferable that the temperature stability is higher than the thermal expansion coefficient of a film-forming material. The thermal expansion coefficient at −30° C. to +70° C. of the glass ceramic according to the present disclosure is normally 70×10.sup.−7/° C. to 95×10.sup.−7/° C., for example, 73×10.sup.−7/° C. to 93×10.sup.−7/° C., or 75×10.sup.−7/° C. to 90×10.sup.−7/° C. The thermal expansion coefficient can be measured by the methods described in the Examples.

[0047] In consideration of harsh usage conditions, it is desired that a glass ceramic for an optical filter resists mechanical deformation. A film of the glass ceramic is formed as a substrate material and then processed into a very small chip shape, so that the glass ceramic needs to have a high Young's modulus. The glass ceramic according to the present disclosure preferably has a Young's modulus of 78 GPa or more. The Young's modulus is more preferably 79 GPa or more, and still more preferably 80 GPa or more. The upper limit of the Young's modulus is normally 95 GPa or less, for example 90 GPa or less. The Young's modulus can be measured by the methods described in the Examples.

[0048] The glass ceramic according to the present disclosure preferably has a Vickers hardness (200 g weight) of 550 to 700. For example, the Vickers hardness is 580 to 650. The abrasion is preferably 50 to 100. For example, the abrasion is 70 to 95. In the glass ceramic of the present disclosure, the hardness is not too hard, the abrasion is not too low, and the workability is excellent. The Vickers hardness and the abrasion can be measured by the methods described in the Examples.

[0049] The glass ceramic according to the present disclosure may be manufactured by the following method. That is, raw materials are uniformly mixed and the mixed raw materials are melted and molded to produce a raw glass. Next, the raw glass is crystallized to manufacture the glass ceramic. Further, the glass ceramic may be used as a base material and a compressive stress layer may be formed to strengthen the glass ceramic.

[0050] The raw glass is subjected to heat treatment to precipitate crystals in the glass. The heat treatment may be performed at a one-stage temperature or a two-stage temperature.

[0051] The two-stage heat treatment includes a nucleation step of firstly treating the raw glass by heat at a first temperature and a crystal growth step of treating, after the nucleation step, the raw glass by heat at a second temperature higher than that in the nucleation step.

[0052] In the one-stage heat treatment, the nucleation step and the crystal growth step are continuously performed at the one-stage temperature. Typically, the temperature is raised to a predetermined heat treatment temperature, is maintained for a certain period of time after reaching the predetermined heat treatment temperature, and is then lowered.

[0053] The first temperature of the two-stage heat treatment is preferably 600° C. to 750° C. A retention time at the first temperature is preferably 30 minutes to 2000 minutes, and more preferably 180 minutes to 1440 minutes.

[0054] The second temperature of the two-stage heat treatment is preferably 650° C. to 850° C. A retention time at the second temperature is preferably 30 minutes to 600 minutes, and more preferably 60 minutes to 300 minutes.

[0055] When the heat treatment is performed at the one-stage temperature, the heat treatment temperature is preferably 600° C. to 800° C., and more preferably 630° C. to 770° C. A retention time at the heat treatment temperature is preferably 30 minutes to 500 minutes, and more preferably 120 minutes to 400 minutes.

[0056] When forming a compressive stress layer on a substrate to increase the strength thereof, means such as grinding and polishing are usually used to form a thin plate-shaped glass ceramic from a glass ceramic. Subsequently, a compressive stress layer is formed on the glass ceramic substrate.

[0057] An example of a method for forming the compressive stress layer includes a chemical strengthening method in which, for example, an alkaline component present in a surface layer of the glass ceramic is subjected to an exchange reaction with an alkaline component having a larger ionic radius to form the compressive stress layer on the surface layer. Other examples include a heat strengthening method in which the glass ceramic is heated and then quenched, and an ion implantation method in which ions are implanted into the surface layer of the glass ceramic.

[0058] The chemical strengthening method may be implemented according to the following steps, for example. A glass-ceramic base material is contacted to or immersed in a salt containing potassium or sodium, for example, a molten salt of potassium nitrate (KNO.sub.3) and sodium nitrate (NaNO.sub.3) or a mixed salt or a complex salt thereof. The treatment of contacting or immersing the glass-ceramic base material to or in the molten salt (chemical strengthening treatment) may be performed in one stage or in two stages.

[0059] For example, in the case of the two-stage chemical strengthening treatment, in a first stage, the glass-ceramic base material is contacted to or immersed in a sodium salt or a mixed salt of potassium and sodium heated at 350° C. to 550° C., for 1 to 1440 minutes, preferably 90 to 800 minutes. Subsequently, in a second stage, the resultant glass-ceramic base material is contacted to or immersed in a potassium salt or a mixed salt of potassium and sodium heated at 350° C. to 550° C., for 1 to 1440 minutes, preferably 60 to 800 minutes.

[0060] In the case of the one-stage chemical strengthening treatment, the glass-ceramic base material is contacted to or immersed in a salt containing potassium or sodium or a mixed salt thereof heated at 350° C. to 550° C. for 1 to 1440 minutes, preferably 60 to 800 minutes.

[0061] In the heat strengthening method it is possible, for example, to heat the glass-ceramic base material to 300° C. to 600° C., and thereafter, perform rapid cooling such as water cooling and/or air cooling to form the compressive stress layer by a temperature difference between the surface and the inside of the glass substrate. When the heat strengthening method is combined with the above chemical treatment method, it is possible to more effectively form the compressive stress layer.

[0062] In the ion implantation method, for example, any type of ion may be caused to collide with the surface of the glass-ceramic base material at an acceleration energy and an acceleration voltage that do not destroy the surface of the base material, to implant the ions into the surface of the base material. Thereafter, by performing heat treatment as necessary, it is possible to form the compressive stress layer on the surface in a similar manner as in the other methods.

[0063] The glass ceramic according to the present disclosure can be used in an optical filter and is suitable for an interference-type optical filter in which a dielectric multilayer film is formed on the surface of a substrate. In particular, the glass ceramic is suitable for a bandpass filter having a structure in which a dielectric thin film (H layer) having a high refractive index and a dielectric thin film (L layer) having a low refractive index are alternately laminated as the dielectric multilayer film.

[0064] The dielectric is preferably an inorganic oxide such as TiO.sub.2, Ta.sub.2O.sub.2, Nb.sub.2O.sub.5, and SiO.sub.2. In a bandpass filter used in a wavelength range of 950 nm to 1600 nm, the dielectric layer preferably has an H layer/L layer combination such as TiO.sub.2/SiO.sub.2, Ta.sub.2O.sub.2/SiO.sub.2, and Nb.sub.2O.sub.5/SiO.sub.2. The optical filter according to the present disclosure can be obtained by forming a dielectric thin film on the surface of a glass-ceramic substrate. Examples of the film forming method include a vapor deposition method, an RF ion plating method, a magnetron sputtering method, and a plasma ion plating method. The vapor deposition method is preferable among the above-mentioned methods.

EXAMPLES

Examples 1 to 5

1. Production of Glass Ceramic

[0065] Raw materials such as oxides, hydroxides, carbonates, nitrates, fluorides, chlorides, and metaphosphate compounds corresponding to each raw material of each component of the glass ceramic were selected, and the selected raw materials were weighed and mixed uniformly to have the following composition ratios.

(Mass % in terms of oxide)
A SiO.sub.2 component was 54%, an Al.sub.2O.sub.3 component was 18%, a Na.sub.2O component was 12%, a K.sub.2O component was 2%, a MgO component was 8%, a CaO component was 1%, a TiO.sub.2 component was 5%, and an Sb.sub.2O.sub.3 component was 0.1%

[0066] Next, the mixed raw materials were fed into and melted in a platinum crucible. Subsequently, the molten glass was stirred and homogenized, cast into a mold, and slowly cooled to prepare raw glass.

[0067] The obtained raw glass was subjected to a one-stage heat treatment (at 665 to 760° C., for five hours) for nucleation and crystallization to produce a glass ceramic. The crystallization temperature in Example 1 was 665° C., the crystallization temperature in Example 2 was 705° C., the crystallization temperature in Example 3 was 720° C., the crystallization temperature in Example 4 was 740° C., and the crystallization temperature in Example 5 was 760° C. The crystal phases were determined from an angle of a peak appearing in an X-ray diffraction pattern obtained by using an X-ray diffraction analyzer (D8 Discover manufactured by Bruker). The main crystal phases of MgAl.sub.2O.sub.4 and MgTi.sub.2O.sub.4 were confirmed.

[0068] The manufactured glass ceramic was cut and ground, and opposing sides of the resultant glass ceramic were further polished in parallel to obtain a glass-ceramic substrate having a thickness of 1 mm.

2. Evaluation of Glass Ceramic

[0069] The following physical characteristics of the obtained glass ceramic were measured. The results are shown in Table 1.

[0070] (1) Internal Transmittance

[0071] According to the Japan Optical Glass Industry Association Standard JOGIS17-2012 “Measuring Method for Internal Transmittance of Optical Glass”, the spectral transmittance including the reflection loss of the glass ceramic after polishing opposing sides in parallel was measured at thicknesses of 1 mm and 10 mm, and the internal transmittance (spectral transmittance not including the reflection loss) of the glass ceramic having a thickness of 1 mm was obtained by calculation.

[0072] (2) Thermal Expansion Coefficient

[0073] The thermal expansion coefficient was obtained from the thermal expansion curve obtained by measuring the relationship between the temperature and the elongation of a sample according to the Japan Optical Glass Industry Association Standard JOGIS16-2003 “Measuring Method for Average Linear Thermal Expansion Coefficient of Optical Glass at Normal Temperature”.

[0074] (3) Young's Modulus

[0075] The Young's modulus was measured by an ultrasonic method.

[0076] (4) Vickers Hardness

[0077] A square pyramid diamond indenter having an angle of 136° between opposing sides was used to measure the Vickers hardness as a value obtained by dividing the load when the pyramid-shaped depression was formed on the test surface by the surface area (mm.sup.2) calculated from the length of the depression.

[0078] The measurement was performed using a microhardness tester MVK-E manufactured by Akashi Seisakusho, Ltd. with a test load of 200 gf and a retention time of 10 seconds.

[0079] (5) Abrasion

[0080] The abrasion was measured according to the Japan Optical Glass Industry Association Standard JOGIS10-1994 “Measuring Method for Abrasion of Optical Glass”. That is, a sample of a glass square plate having a size of 30×30×10 mm was placed at a fixed position 80 mm from the center of a cast iron flat plate (250 mm φ) rotating horizontally 60 times per minute. While applying a vertical load of 9.8 N (1 kgf), a polishing solution obtained by adding 10 g of #800 (average particle diameter of 20 μm) lapping material (alumina A abrasive grains) to 20 mL of water was uniformly supplied for 5 minutes to rub the glass square plate. Finally, the sample mass before and after lapping was measured to determine the wear mass. Similarly, the wear mass of a standard sample specified by the Japan Optical Glass Industry Association was determined, and the abrasion was calculated by:

Abrasion={(Wear mass/specific gravity of test sample)/(Wear mass/specific gravity of standard sample)}×100.

Comparative Example 1

[0081] A glass ceramic was produced and evaluated similarly as in Example 1, except that the composition of the glass ceramic was changed as described below and the crystallization temperature was set to 750° C. The results are shown in Table 1.

(Mass % in terms of oxide)
A SiO.sub.2 component was 76.0%, an Al.sub.2O.sub.3 component was 6.4%, a P.sub.2O.sub.5 component was 2.0%, a ZrO.sub.2 component was 3.0%, a ZnO component was 0.6%, a MgO component was 0.5%, a CaO component was 0.3%, a Li.sub.2O component was 10.0%, a K.sub.2O component was 1.0%, and an Sb.sub.2O.sub.3 component was 0.2%.

Comparative Example 2

[0082] A glass was produced and evaluated similarly to Example 1, except that the composition of the glass was changed as described below and the glass was not crystallized. The results are shown in Table 1.

(Mass % in terms of oxide)
A SiO.sub.2 component was 65.0%, a B.sub.2O.sub.3 component was 13.6%, an Al.sub.2O.sub.3 component was 2.0%, a ZnO component was 1.5%, a BaO component was 3.0%, a Na.sub.2O component was 7.4%, a K.sub.2O component was 7.0%, and an Sb.sub.2O.sub.3 component was 0.5%.

TABLE-US-00001 TABLE 1 Examples Comparative Comparative 1 2 3 4 5 Example 1 Example 2 Internal 320 0.010 0.010 0.564 0.978 transmittance 350 0.785 0.786 0.610 0.990 (τ/1 mmt) 400 0.961 0.961 0.001 0.001 0.001 0.692 0.994 440 0.967 0.968 0.002 0.002 0.002 0.758 0.994 500 0.971 0.972 0.012 0.012 0.012 0.831 0.995 550 0.977 0.977 0.056 0.056 0.056 0.873 0.995 600 0.983 0.984 0.151 0.151 0.151 0.903 0.995 650 0.990 0.990 0.281 0.281 0.281 0.925 0.995 700 0.994 0.994 0.415 0.415 0.416 0.941 0.995 800 0.997 0.998 0.636 0.636 0.637 0.962 0.992 900 0.999 0.999 0.774 0.774 0.775 0.975 0.999 1000 0.999 0.999 0.859 0.859 0.860 0.982 0.999 1200 0.999 0.999 0.939 0.939 0.940 0.990 0.999 1400 0.999 0.999 0.965 0.965 0.966 0.994 0.999 1500 0.999 0.999 0.978 0.978 0.979 0.999 0.999 1550 0.999 0.999 0.980 0.980 0.981 0.996 0.999 1600 0.999 0.999 0.983 0.983 0.985 0.996 0.999 1800 0.999 0.999 0.987 0.987 0.988 0.997 0.999 2000 0.999 0.999 0.990 0.990 0.991 0.997 0.999 2200 0.999 0.999 0.956 0.956 0.957 0.994 0.997 2400 0.999 0.999 0.959 0.959 0.961 0.995 0.990 Thermal expansion (−30 to +70) 81 79 79 80 85 101 67 coefficient (10.sup.−7/° C.) Young's modulus (GPa) 80.6 80.6 81.0 83.0 84.3 97.4 76.5 Vickers hardness (200 g Hv_200 gf 619 626 622 616 621 755 613 weight) Abrasion Aa 78 — 86 86 — 31 88
The documents described in this specification and the entire disclosure (including description, drawings, and claims) of the Japanese patent application specification, which is the basis for the priority of the present application under the Paris Convention, are incorporated herein by reference.