CHALCOGENIDE GLASS MATERIAL

Abstract

Provided is a small-diameter chalcogenide glass material having excellent weather resistance and mechanical strength and being suitable as an optical element for an infrared sensor. The chalcogenide glass material has an unpolished side surface, a pillar shape with a diameter of 15 mm or less, and a composition of, in terms of % by mole, 40 to 90% S+Se+Te and an inside of the glass material is free of stria with a length of 500 μm or more.

Description

TECHNICAL FIELD

The present invention relates to chalcogenide glass materials for use in infrared sensors, infrared cameras, and so on.

BACKGROUND ART

Vehicle-mounted night vision devices, security systems, and the like include infrared sensors for use to detect living bodies at night. To sense infrared rays with wavelengths of about 8 to 14 μm emitted from living bodies, such an infrared sensor is provided, in front of the sensor part, with an optical element, such as a filter or a lens, capable of transmitting infrared rays in the above wavelength range.

Examples of a material for the optical element as described above include Ge, Zn, and Se. These materials are crystalline bodies and therefore have poor processability, which makes them difficult to process into complicated shapes, such as an aspheric lens. For this reason, these materials have the problem of making mass production of the above optical element difficult and also have the problem of making size reduction of the infrared sensor difficult.

To cope with the above, chalcogenide glasses are proposed as vitreous materials that can transmit infrared rays with wavelengths of about 8 to 14 μm and are relatively easily processable (see, for example, Patent Literature 1).

Recently, a small-diameter chalcogenide glass has been desired for the purpose of further size reduction of infrared sensors.

CITATION LIST

Patent Literature

• [PTL 1] JP-A-2009-161374

SUMMARY OF INVENTION

Technical Problem

However, a small-diameter chalcogenide glass has poor weather resistance and mechanical strength. Furthermore, when the chalcogenide glass is used as an optical element for an infrared sensor, there arises a problem that an image is distorted or disturbed.

The present invention has been made in view of the above situations and, therefore, has an object of providing a small-diameter chalcogenide glass material having excellent weather resistance and mechanical strength and being suitable as an optical element for an infrared sensor.

Solution to Problem

The inventors have conducted various studies, consequently have made the following findings, and have proposed the present invention based on the findings. A small-diameter chalcogenide glass material is typically produced by cutting and polishing. When the side surface of the chalcogenide glass is polished, microscopic polishing flaws are formed in the side surface, so that the specific surface area of the side surface increases. As a result, the area of contact of the chalcogenide glass with outside air increases and, therefore, the weather resistance becomes likely to decrease. Furthermore, small defects called Griffith flaws are produced by the polishing process, so that the mechanical strength becomes likely to decrease. Meanwhile, when producing a small-diameter chalcogenide glass material, striae are likely to be produced in the glass material. If there is a large-sized stria in the chalcogenide glass material, images from the infrared sensor are likely to be distorted or disturbed.

A chalcogenide glass material according to the present invention is a chalcogenide glass material having an unpolished side surface, a pillar shape with a diameter of 15 mm or less, and a composition of, in terms of % by mole, 40 to 90% S+Se+Te, an inside of the glass material being free of stria with a length of 500 μm or more.

Since the side surface is unpolished, the specific surface area is reduced, which makes the weather resistance likely to be increased, and no Griffith flaw decreasing the mechanical strength is produced, which makes the mechanical strength likely to be increased. Furthermore, since there is no stria with a length of 500 μm or more in the glass material, images from an infrared sensor are less likely to be distorted or disturbed.

In the chalcogenide glass material according to the present invention, the side surface is preferably a fire-polished surface. Since the side surface is formed into a fire-polished surface, the specific surface area is further reduced, so that the weather resistance and mechanical strength are more likely to be increased.

The chalcogenide glass material according to the present invention preferably contains, in terms of % by mole, over 0 to 50% Ge+Ga+Sb+As.

The chalcogenide glass material according to the present invention preferably contains, in terms of % by mole, 0 to 40% Ge+Ga and 0 to 45% Sb+As.

A method for producing a chalcogenide glass material according to the present invention includes drawing a glass base material containing, in terms of % by mole, 40 to 90% S+Se+Te by a redraw process. Since the glass base material is redrawn, an unpolished, small-diameter chalcogenide glass can be easily obtained.

In the method for producing a chalcogenide glass material according to the present invention, a drawing temperature is preferably equal to or lower than a glass transition point of the chalcogenide glass plus 100° C. Since the drawing temperature is equal to or lower than the glass transition point of the chalcogenide glass plus 100° C., the evaporation of the glass components can be reduced, so that striae are less likely to be produced.

In the method for producing a chalcogenide glass material according to the present invention, the drawing is preferably performed in a vacuum or in an inert atmosphere. Since the drawing is performed in a vacuum or in an inert atmosphere, the evaporation of the glass components can be further reduced, so that striae are even less likely to be produced.

An optical element according to the present invention uses the above-described chalcogenide glass material.

An infrared sensor according to the present invention uses the above-described optical element.

Advantageous Effects of Invention

The present invention enables provision of a small-diameter chalcogenide glass material having excellent weather resistance and mechanical strength and being suitable as an optical element for an infrared sensor.

BRIEF DESCRIPTION OF DRAWINGS

FIG. 1 is a photograph showing the inside of a sample obtained in Example 1.

FIG. 2 is a photograph showing the inside of a sample obtained in Comparative Example 1.

DESCRIPTION OF EMBODIMENTS

A chalcogenide glass material according to the present invention has an unpolished side surface and, particularly, the side surface is preferably a fire-polished surface. If the side surface is polished, the specific surface area of the side surface increases, so that the reaction with oxygen and moisture in the air is promoted, which makes the weather resistance likely to be decreased. Furthermore, small defects called Griffith flaws are produced by the polishing process, so that the mechanical strength is likely to be decreased. If a polishing step is included in the production process, a problem of cost rise also arises.

The chalcogenide glass material according to the present invention has a pillar shape and its diameter is 15 mm or less, preferably 10 mm or less, and particularly preferably 5 mm or less. If the diameter is too large, this makes it difficult to reduce the size of an infrared sensor. Although no particular limitation is placed on the lower limit of the diameter, it is realistically 1 mm or more.

The chalcogenide glass material according to the present invention is free of stria with a length of 500 μm or more. Even if there are striae in the chalcogenide glass material, their lengths are less than 500 μm, preferably 200 μm or less, more preferably 100 μm or less, still more preferably 50 μm or less, and particularly preferably 10 μm or less. By doing so, when the chalcogenide glass material is used as an optical element, the reduction in resolution of an image due to distortion or disturbance can be prevented.

The chalcogenide glass material according to the present invention contains, in terms of % by mole, 40 to 90% S+Se+Te. Reasons why the glass composition is limited as just described will be described below. Note that in the following description of the contents of components “%” refers to “% by mole” unless otherwise specified.

Chalcogen elements, S, Se, and Te, are components for forming the glass network. The content of S+Se+Te (the total amount of S, Se, and Te) is 40 to 90%, preferably 50 to 80%, more preferably 50 to 65%, and particularly preferably 55 to 65%. If the content of S+Se+Te is too small, vitrification becomes difficult. On the other hand, if the content of S+Se+Te is too large, the glass components are likely to evaporate during melting and redrawing, which is likely to cause striae.

The chalcogenide glass material may contain, in addition to the above components, the various components mentioned below.

Ge, Ga, Sb, and As are components that widen the vitrification range and increase the thermal stability of glass. Ge+Ga+Sb+As (the total amount of Ge, Ga, Sb, and As) is preferably over 0 to 50%, more preferably 10 to 45%, still more preferably 15 to 43%, yet still more preferably 20 to 43%, even still more preferably 25 to 43%, and particularly preferably 30 to 43%. If the content of Ge+Ga+Sb+As is too large, vitrification becomes difficult.

Ge+Ga (the total amount of Ge and Ga) is preferably 0 to 40%, more preferably 2 to 35%, still more preferably 4 to 33%, yet still more preferably 4 to 30%, even still more preferably 4 to 28%, and particularly preferably 4 to 25%. Sb+As (the total amount of Sb and As) is preferably 0 to 45%, more preferably 5 to 40%, still more preferably 10 to 35%, yet still more preferably 15 to 35%, and particularly preferably 20 to 35%.

The chalcogenide glass material having the above composition is likely to exhibit a glass transition point of 100 to 400° C., 120 to 380° C., or particularly 140 to 360° C.

Next, a description will be given of a method for producing a chalcogenide glass material according to the present invention. The chalcogenide glass material according to the present invention can be produced by Production Method 1 below.

(Production Method 1)

Raw materials are mixed to give the above-described glass composition, thus obtaining a raw material batch. Next, a quartz glass ampoule is evacuated with the application of heat, the raw material batch is then put into the quartz glass ampoule, and the quartz glass ampoule is sealed with an oxygen burner while being evacuated. Note that the diameter of the quartz glass ampoule is preferably 15 mm or more, more preferably 17 mm or more, and particularly preferably 20 mm or more. If the diameter of the quartz glass ampoule is too small, a melt is difficult to move in the quartz glass ampoule, so that a stirring effect cannot sufficiently be obtained and striae are therefore likely to be produced.

Next, the sealed quartz glass ampoule is raised in temperature to 650 to 1000° C. at a rate of 10° C. to 20° C./hour in a melting furnace and then held for six to twelve hours. During the holding time, the quartz glass ampoule is turned upside down as necessary to stir the melt.

Subsequently, the quartz glass ampoule is taken out of the melting furnace and rapidly cooled to room temperature, thus obtaining a glass base material. Thereafter, the quartz glass ampoule is cut and the glass base material is taken out of the ampoule.

When the obtained glass base material is drawn by a redraw process, a pillar-like chalcogenide glass material having a smaller diameter can be obtained. The side surface of the chalcogenide glass material produced by the redraw process is a fire-polished surface, which has excellent weather resistance and mechanical strength.

The drawing temperature is preferably equal to or lower than the glass transition point of the chalcogenide glass material plus 100° C., more preferably equal to or lower than the glass transition point of the chalcogenide glass material plus 80° C., still more preferably equal to or lower than the glass transition point of the chalcogenide glass material plus 60° C., and particularly preferably equal to or lower than the glass transition point of the chalcogenide glass material plus 40° C. If the drawing temperature is too high, the glass components easily evaporate, so that striae are likely to be produced and the refractive index of the inside of the glass material is likely to be uneven. The atmosphere in which the drawing is performed is preferably a vacuum or an inert atmosphere. The preferred inert atmosphere is nitrogen, argon or helium atmosphere. Particularly preferred is a nitrogen atmosphere because of its inexpensiveness. If the drawing is performed without controlling the atmosphere, components in the chalcogenide glass material react with oxygen in the air, so that the evaporation of glass components is promoted. For example, in the case of a sulfide-based chalcogenide glass material containing much sulfur, sulfur in the glass material reacts with oxygen, so that SO₂ evaporates from the surface of the glass material. Thus, striae are likely to be produced and the refractive index of the inside of the glass material is likely to be uneven. In addition, the glass material may be oxidized, so that its infrared transparency tends to decrease.

As alternatives to Production method 1, a chalcogenide glass material may be produced by Production Method 2 or 3 below.

(Production Method 2)

Raw materials are mixed to give the above-described glass composition, thus obtaining a raw material batch. Next, a quartz glass ampoule is evacuated with the application of heat, the raw material batch is then put into the quartz glass ampoule, and the quartz glass ampoule is sealed with an oxygen burner while being evacuated. Note that the diameter of the quartz glass ampoule is the same as described above.

Next, the sealed quartz glass ampoule is raised in temperature to 650 to 1000° C. at a rate of 10° C. to 20° C./hour in a melting furnace and then held for six to twelve hours. During the holding time, the quartz glass ampoule is turned upside down as necessary to stir the melt.

Next, the quartz glass ampoule is taken out of the melting furnace and the melt is poured into a mold in an inert atmosphere and rapidly cooled to room temperature, thus obtaining a chalcogenide glass material. Thereafter, the obtained chalcogenide glass material may be drawn by a redraw process. The material for the mold is preferably carbon or quartz glass . If a metallic mold is used, it may react with the melt to form an alloy. Because the diameter of the chalcogenide glass material depends on the inner diameter of the mold, the inner diameter of the mold should be selected according to the diameter of a chalcogenide glass material to be produced.

(Production Method 3)

Raw materials are mixed to give the above-described glass composition, thus obtaining a raw material batch. Next, a quartz glass ampoule is evacuated with the application of heat, the raw material batch is then put into the quartz glass ampoule, and the quartz glass ampoule is sealed with an oxygen burner while being evacuated. The quartz glass ampoule preferably has a shape in which a glass forming portion for glass formation with an inner diameter of 15 mm or less is connected to a stirring portion for stirring with an inner diameter of 15 mm or more. Thus, during stirring, the melt flows into the stirring portion and thus can easily move in the quartz glass ampoule. Note that the inner diameter of the glass forming portion should be selected according to the diameter of a chalcogenide glass material to be produced.

Next, the sealed quartz glass ampoule is raised in temperature to 650 to 1000° C. at a rate of 10° C. to 20° C./hour in a melting furnace and then held for six to twelve hours. During the holding time, the quartz glass ampoule is turned upside down as necessary to stir the melt.

Subsequently, the quartz glass ampoule is taken out of the melting furnace and the melt is moved to the glass forming portion and rapidly cooled to room temperature, thus obtaining a chalcogenide glass material.

Since the chalcogenide glass material according to the present invention has excellent weather resistance and mechanical strength and is free of stria of 500 μm or more which may cause image distortion or disturbance, it is suitable as an optical element, such as a lens for focusing infrared light on an infrared sensor part of an infrared camera.

EXAMPLES

Hereinafter, the present invention will be described with reference to examples, but is not limited to the examples.

Tables 1 to 16 show Examples 1 to 180 according to the present invention and Comparative Examples 1 and 2.

	TABLE 1
	Example
	1	2	3	4	5	6	7	8	9	10	11	12
Glass	Ge	28.0	5.0
composition	Ga
(% by mole)	Sb	12.0	33.0
	As
	S		61.0
	Se	60.0
	Te
	Bi		1.0
	Sn
Glass transition point	278	230
(° C.)
Diameter of glass base	15	15	15	15	21	30	15	15	15	15	21	30
material (mm)
Diameter of chalcogenide	3.0	5.0	7.0	9.0	11.0	13.0	3.0	5.0	7.0	9.0	11.0	13.0
glass material (mm)
Striae	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯

	TABLE 2
	Example
	13	14	15	16	17	18	19	20	21	22	23	24
Glass	Ge	22.0	33.0
composition	Ga
(% by mole)	Sb
	As	20.0	12.0
	S
	Se	58.0	55.0
	Te
	Bi
	Sn
Glass transition point	292	368
(° C.)
Diameter of glass base	15	15	15	15	21	30	15	15	15	15	21	30
material (mm)
Diameter of chalcogenide	3.0	5.0	7.0	9.0	11.0	13.0	3.0	5.0	7.0	9.0	11.0	13.0
glass material (mm)
Striae	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯

	TABLE 3
	Example
	25	26	27	28	29	30	31	32	33	34	35	36
Glass	Ge	30.0	10.0
composition	Ga
(% by mole)	Sb
	As	13.0	40.0
	S
	Se	32.0	50.0
	Te	25.0
	Bi
	Sn
Glass transition point	275	225
(° C.)
Diameter of glass base	15	15	15	15	21	30	15	15	15	15	21	30
material (mm)
Diameter of chalcogenide	3.0	5.0	7.0	9.0	11.0	13.0	3.0	5.0	7.0	9.0	11.0	13.0
glass material (mm)
Striae	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯

	TABLE 4
	Example
	37	38	39	40	41	42	43	44	45	46	47	48
Glass	Ge
composition	Ga
(% by mole)	Sb
	As	40.0	40.0
	S		60.0
	Se	60.0
	Te
	Bi
	Sn
Glass transition point	185	197
(° C.)
Diameter of glass base	15	15	15	15	21	30	15	15	15	15	21	30
material (mm)
Diameter of chalcogenide	3.0	5.0	7.0	9.0	11.0	13.0	3.0	5.0	7.0	9.0	11.0	13.0
glass material (mm)
Striae	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯

	TABLE 5
	Example
	49	50	51	52	53	54	55	56	57	58	59	60
Glass	Ge
composition	Ga	20.0	8.2
(% by mole)	Sb		27.7
	As
	S		59.0
	Se
	Te	80.0
	Bi
	Sn		5.1
Glass transition point	147	239
(° C.)
Diameter of glass base	15	15	15	15	21	30	15	15	15	15	21	30
material (mm)
Diameter of chalcogenide	3.0	5.0	7.0	9.0	11.0	13.0	3.0	5.0	7.0	9.0	11.0	13.0
glass material (mm)
Striae	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯

	TABLE 6
	Example
	61	62	63	64	65	66	67	68	69	70	71	72
Glass	Ge	28.0	5.0
composition	Ga
(% by mole)	Sb	12.0	33.0
	As
	S		61.0
	Se	60.0
	Te
	Bi		1.0
	Sn
Glass transition point	278	230
(° C.)
Diameter of chalcogenide	3.0	5.0	7.0	9.0	11.0	13.0	3.0	5.0	7.0	9.0	11.0	13.0
glass material (mm)
Striae	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯

	TABLE 7
	Example
	73	74	75	76	77	78	79	80	81	82	83	84
Glass	Ge	22.0	33.0
composition	Ga
(% by mole)	Sb
	As	20.0	12.0
	S
	Se	58.0	55.0
	Te
	Bi
	Sn
Glass transition point	292	368
(° C.)
Diameter of chalcogenide	3.0	5.0	7.0	9.0	11.0	13.0	3.0	5.0	7.0	9.0	11.0	13.0
glass material (mm)
Striae	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯

	TABLE 8
	Example
	85	86	87	88	89	90	91	92	93	94	95	96
Glass	Ge	30.0	10.0
composition	Ga
(% by mole)	Sb
	As	13.0	40.0
	S
	Se	32.0	50.0
	Te	25.0
	Bi
	Sn
Glass transition point	275	225
(° C.)
Diameter of chalcogenide	3.0	5.0	7.0	9.0	11.0	13.0	3.0	5.0	7.0	9.0	11.0	13.0
glass material (mm)
Striae	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯

	TABLE 9
	Example
	97	98	99	100	101	102	103	104	105	106	107	108
Glass	Ge
composition	Ga
(% by mole)	Sb
	As	40.0	40.0
	S		60.0
	Se	60.0
	Te
	Bi
	Sn
Glass transition point	185	197
(° C.)
Diameter of chalcogenide	3.0	5.0	7.0	9.0	11.0	13.0	3.0	5.0	7.0	9.0	11.0	13.0
glass material (mm)
Striae	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯

	TABLE 10
	Example
	109	110	111	112	113	114	115	116	117	118	119	120
Glass	Ge
composition	Ga	20.0	8.2
(% by mole)	Sb		27.7
	As
	S		59.0
	Se
	Te	80.0
	Bi
	Sn		5.1
Glass transition point	147	239
(° C.)
Diameter of chalcogenide	3.0	5.0	7.0	9.0	11.0	13.0	3.0	5.0	7.0	9.0	11.0	13.0
glass material (mm)
Striae	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯

	TABLE 11
	Example
	121	122	123	124	125	126	127	128	129	130	131	132
Glass	Ge	28.0	5.0
composition	Ga
(% by mole)	Sb	12.0	33.0
	As
	S		61.0
	Se	60.0
	Te
	Bi		1.0
	Sn
Glass transition point	278	230
(° C.)
Inner diameter of	15	15	15	15	21	30	15	15	15	15	21	30
stirring portion (mm)
Inner diameter of	3.0	5.0	7.0	9.0	11.0	13.0	3.0	5.0	7.0	9.0	11.0	13.0
forming portion (mm)
Diameter of chalcogenide	3.0	5.0	7.0	9.0	11.0	13.0	3.0	5.0	7.0	9.0	11.0	13.0
glass material (mm)
Striae	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯

	TABLE 12
	Example
	133	134	135	136	137	138	139	140	141	142	143	144
Glass	Ge	22.0	33.0
composition	Ga
(% by mole)	Sb
	As	20.0	12.0
	S
	Se	58.0	55.0
	Te
	Bi
	Sn
Glass transition point	292	368
(° C.)
Inner diameter of	15	15	15	15	21	30	15	15	15	15	21	30
stirring portion (mm)
Inner diameter of	3.0	5.0	7.0	9.0	11.0	13.0	3.0	5.0	7.0	9.0	11.0	13.0
forming portion (mm)
Diameter of chalcogenide	3.0	5.0	7.0	9.0	11.0	13.0	3.0	5.0	7.0	9.0	11.0	13.0
glass material (mm)
Striae	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯

	TABLE 13
	Example
	145	146	147	148	149	150	151	152	153	154	155	156
Glass	Ge	30.0	10.0
composition	Ga
(% by mole)	Sb
	As	13.0	40.0
	S
	Se	32.0	50.0
	Te	25.0
	Bi
	Sn
Glass transition point	275	225
(° C.)
Inner diameter of	15	15	15	15	21	30	15	15	15	15	21	30
stirring portion (mm)
Inner diameter of	3.0	5.0	7.0	9.0	11.0	13.0	3.0	5.0	7.0	9.0	11.0	13.0
forming portion (mm)
Diameter of chalcogenide	3.0	5.0	7.0	9.0	11.0	13.0	3.0	5.0	7.0	9.0	11.0	13.0
glass material (mm)
Striae	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯

	TABLE 14
	Example
	157	158	159	160	161	162	163	164	165	166	167	168
Glass	Ge
composition	Ga
(% by mole)	Sb
	As	40.0	40.0
	S		60.0
	Se	60.0
	Te
	Bi
	Sn
Glass transition point	185	197
(° C.)
Inner diameter of	15	15	15	15	21	30	15	15	15	15	21	30
stirring portion (mm)
Inner diameter of	3.0	5.0	7.0	9.0	11.0	13.0	3.0	5.0	7.0	9.0	11.0	13.0
forming portion (mm)
Diameter of chalcogenide	3.0	5.0	7.0	9.0	11.0	13.0	3.0	5.0	7.0	9.0	11.0	13.0
glass material (mm)
Striae	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯

	TABLE 15
	Example
	169	170	171	172	173	174	175	176	177	178	179	180
Glass	Ge
composition	Ga	20.0	8.2
(% by mole)	Sb		27.7
	As
	S		59.0
	Se
	Te	80.0
	Bi
	Sn		5.1
Glass transition point	147	239
(° C.)
Inner diameter of	15	15	15	15	21	30	15	15	15	15	21	30
stirring portion (mm)
Inner diameter of	3.0	5.0	7.0	9.0	11.0	13.0	3.0	5.0	7.0	9.0	11.0	13.0
forming portion (mm)
Diameter of chalcogenide	3.0	5.0	7.0	9.0	11.0	13.0	3.0	5.0	7.0	9.0	11.0	13.0
glass material (mm)
Striae	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯	◯

	TABLE 16
	Comparative Example
	1	2
Glass	Ge	5.0	4.0
composition	Ga
(% by mole)	Sb	33.0	4.0
	As
	S	61.0
	Se		92.0
	Te
	Bi	1.0
	Sn
Glass transition point (° C.)	230	248
Diameter of glass base material (mm)	—	15
Diameter of chalcogenide glass material (mm)	5.0	5.0
Striae	X	X

Samples in Examples 1 to 60 and a sample in Comparative Example 2 were produced in the following manner. Raw materials were mixed to give each composition shown in the tables, thus obtaining a raw material batch. Next, a 15-30 mm inner diameter quartz glass ampoule washed in pure water was evacuated with the application of heat, the raw material batch was then put into the quartz glass ampoule, and the quartz glass ampoule was sealed with an oxygen burner while being evacuated. The sealed quartz glass ampoule was raised in temperature to 650 to 1000° C. at a rate of 10 to 20° C./hour in a melting furnace and then held for six to twelve hours. During the holding time, the quartz glass ampoule was turned upside down every two hours to stir the melt. Thereafter, the quartz glass ampoule was taken out of the melting furnace and rapidly cooled to room temperature, thus obtaining a columnar glass base material having a diameter shown in the table.

The obtained glass base material was heated to a temperature 30 to 50° C. higher than the glass transition point in a nitrogen atmosphere and drawn by a redraw process, thus obtaining a columnar chalcogenide glass material having a diameter shown in the table.

Samples in Examples 61 to 120 were produced in the following manner. Raw materials were mixed to give each composition shown in the tables, thus obtaining a raw material batch. Next, a 15-50 mm inner diameter quartz glass ampoule washed in pure water was evacuated with the application of heat, the raw material batch was then put into the quartz glass ampoule, and the quartz glass ampoule was sealed with an oxygen burner while being evacuated. The sealed quartz glass ampoule was raised in temperature to 650 to 1000° C. at a rate of 10 to 20° C./hour in a melting furnace and then held for six to twelve hours. During the holding time, the quartz glass ampoule was turned upside down every two hours to stir the melt. Thereafter, the quartz glass ampoule was taken out of the melting furnace, a portion thereof was cut in a nitrogen atmosphere, and the melt was poured into a carbon-made mold and rapidly cooled to room temperature, thus obtaining a columnar chalcogenide glass material having a diameter shown in the table.

Samples in Examples 121 to 180 were produced in the following manner. Raw materials were mixed to give each composition shown in the tables, thus obtaining a raw material batch. Next, a quartz glass ampoule washed in pure water was evacuated with the application of heat, the raw material batch was then put into the quartz glass ampoule, and the quartz glass ampoule was sealed with an oxygen burner while being evacuated. The sealed quartz glass ampoule having an inner diameter of a stirring portion and an inner diameter of a forming portion each shown in the table was raised in temperature to 650 to 1000° C. at a rate of 10 to 20° C./hour in a melting furnace and then held for six to twelve hours. During the holding time, the quartz glass ampoule was turned upside down every two hours to stir the melt. Thereafter, the quartz glass ampoule was taken out of the melting furnace and the melt was moved to the forming portion and rapidly cooled to room temperature, thus obtaining a columnar chalcogenide glass material having a diameter shown in the table.

Comparative Example 1 was produced in the following manner. Raw materials were mixed to give a composition shown in the table, thus obtaining a raw material batch. Next, a 5 mm inner diameter quartz glass ampoule washed in pure water was evacuated with the application of heat, the raw material batch was then put into the quartz glass ampoule, and the quartz glass ampoule was sealed with an oxygen burner while being evacuated. The sealed quartz glass ampoule was raised in temperature to 800° C. at a rate of 15° C./hour in a melting furnace and then held for ten hours. During the holding time, the quartz glass ampoule was turned upside down every two hours to stir the melt. Thereafter, the quartz glass ampoule was taken out of the melting furnace and rapidly cooled to room temperature, thus obtaining a chalcogenide glass material.

The obtained samples were measured or evaluated in terms of glass transition point and striae.

The glass transition point was measured with a TMA (thermo-mechanical analyzer).

Striae were evaluated in the following manner. The inside of each of the obtained samples was observed by a shadow graph method using infrared light with a wavelength of 1 μm. Samples in which striae with a length of 500 μm or more were observed are indicated by a “circle” sign, whereas samples in which no stria with a length of 500 μm or more was observed are indicated by a “cross” sign. FIG. 1 shows a photograph of the inside of the sample in Example 1. FIG. 2 shows a photograph of the inside of the sample in Comparative Example 1.

No stria with a length of 500 μm or more was observed in the samples in Examples 1 to 180 and, therefore, these samples exhibited excellent homogeneity. In addition, since these samples were unpolished, they can be considered to have excellent weather resistance and mechanical strength. On the other hand, striae with a length of 500 μm or more were observed in the samples in Comparative Examples 1 and 2 and, therefore, these samples exhibited poor homogeneity.

INDUSTRIAL APPLICABILITY

The chalcogenide glass material according to the present invention is suitable as an optical element, such as a lens for focusing infrared light on an infrared sensor part of an infrared camera.

Claims

1. A chalcogenide glass material having an unpolished side surface, a pillar shape with a diameter of 15 mm or less, and a composition of, in terms of % by mole, 40 to 90% S+Se+Te, an inside of the glass material being free of stria with a length of 500 μm or more.

2. The chalcogenide glass material according to claim 1, wherein the side surface is a fire-polished surface.

3. The chalcogenide glass material according to claim 1, containing, in terms of % by mole, over 0 to 50% Ge+Ga+Sb+As.

4. The chalcogenide glass material according to claim 1, containing, in terms of % by mole, 0 to 40% Ge+Ga and 0 to 45% Sb+As.

5. A method for producing a chalcogenide glass material, the method comprising drawing a glass base material containing, in terms of % by mole, 40 to 90% S+Se+Te by a redraw process.

6. The method for producing a chalcogenide glass material according to claim 5, wherein a drawing temperature is equal to or lower than a glass transition point of the chalcogenide glass material plus 100° C.

7. The method for producing a chalcogenide glass material according to claim 5, wherein the drawing is performed in a vacuum or in an inert atmosphere.

8. An optical element using the chalcogenide glass material according to claim 1.

9. An infrared sensor using the optical element according to claim 8.