GB2031399A - Creación de Inventos y Patentes con Inteligencia Artificial

GB2031399A – Polycrystalline transparent spinel sintered body
– Google Patents

GB2031399A – Polycrystalline transparent spinel sintered body
– Google Patents
Polycrystalline transparent spinel sintered body

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Publication number
GB2031399A

GB2031399A
GB7927727A
GB7927727A
GB2031399A
GB 2031399 A
GB2031399 A
GB 2031399A
GB 7927727 A
GB7927727 A
GB 7927727A
GB 7927727 A
GB7927727 A
GB 7927727A
GB 2031399 A
GB2031399 A
GB 2031399A
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United Kingdom
Prior art keywords
sintered body
mgo
mixture
spinel sintered
polycrystalline transparent
Prior art date
1978-08-14
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GB7927727A
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GB2031399B
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NGK Insulators Ltd

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NGK Insulators Ltd
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1978-08-14
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1979-08-09
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1980-04-23

1979-08-09
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NGK Insulators Ltd

1980-04-23
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patent/GB2031399A/en

1982-08-11
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1982-08-11
Publication of GB2031399B
publication
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patent/GB2031399B/en

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Classifications

C—CHEMISTRY; METALLURGY

C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES

C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE

C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products

C04B35/01—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics

C04B35/10—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on aluminium oxide

C04B35/111—Fine ceramics

C04B35/115—Translucent or transparent products

C—CHEMISTRY; METALLURGY

C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES

C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE

C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products

C04B35/44—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on aluminates

C04B35/443—Magnesium aluminate spinel

Description

1
SPECIFICATION Polycrystalline transparent spinel sintered body and a method of producing the same
GB 2 031 399 A 1 The present invention relates to a polycrystalline transparent spinel sintered body and to a method of producing the same.
A transparent spinel sintered body consisting mainly of aluminium oxide and magnesium oxide 5 has a cubic system crystal structure, and is free from double refaction. Therefore, the transparent spine] sintered body has excellent light transmission in the visible and infrared spectra.
The following methods of producing polycrystalline transparent spinel sintered bodies have hitherto been known.
(1) A stoichiometric mixture of A120, and MgO is hot pressed.
(2) A stoichiometric powdery mixture of A1,0, and MgO is fired together with calcium oxide (CaO) or magnesium oxide (MgO).
(3) A powdery mixture of A’203 and a stoichiometric excess of MgO for spinel is fired together with more than 0.2% by weight of LiF.
(4) An alumina single crystal (sapphire) or polyerystalline high-density alumina sintered body is 15 contacted with MgO vapour to form a spinel.
However, these methods have the following drawbacks. That is, in the method (1) of hot pressing a stoichiometric mixture of A120. and MgO, a die made of carbon is used, and therefore the resulting sintered body is always a dark sintered body having a simple shape, and moreover, the sintered body is expensive to produce due to the low productivity of the method. In the method (2) of firing a stoichiometric powdery mixture of A1203 and MgO together with CaO or MgO, and in the method (3) of firing a powdery mixture of A120, and a stoichiometric excess of MgO for spinel together with more than 0.2% by weight of LiF, a relatively large amount of additive must be used, and therefore the resulting sintered body has a poor purity and a poor light transmittance. In the method (4) of contacting an alumina single crystal or polycrystalline alumina sintered body with MgO vapour, it is very difficult to control the amount of MgO vapour, and hence the production of a homogeneous sintered body is difficult.
The present invention in one aspect provides a polycrystalline transparent spinel sintered body consisting mainly of A1,0, and MgO in a molar ratio of A1,0,/MgO of from 0.52/0.48 to 0.70/0.30, and containing 0.001-0.1% by weight of UR The invention in another aspect provides a method of producing a polycrystalline transparent spinel sintered body, comprising mixing A1,0, with MgO, or mixing an aluminium compound with a magnesium compound which are respectively formed into A1,0, and MgO by calcination, in a molar ratio of A120M90 of from 0.50/0.50 to 0.525/0.475, calcining the mixture of 1,1 50-1,300’C, mixing the calcined mixture with 0.01—0.2% by weight of LiF based on the amount of the calcined 35 mixture, moulding the resulting mixture into a given shape, and subjecting the resulting shaped article to a primary firing at 1,200-1,4001C and then a secondary firing at 1,700- 1,9001C under a hydrogen atmosphere, a vacuum or an inert gas atmosphere, wherein the rate of temperature increase is not highpr than 1 001C/hr within the temperature range between the primary firing step and the secondary firing step.
In particular, the present invention is based on the discovery that, when a raw material powder containing alumina in an amount slightly larger than the stoichiometric amount for spinel and further containing a specifically limited amount of LiF is fired under specifically limited condifiOns, thb raw material powder can be formed into a sintered body having a density higher than that of conventional sintered bodies at a temperature lower than the firing temperature in conventional methods and a spinel 45 sintered body having an excellent light transmittance can be obtained.
The method according to the present invention of producing a polycrystalline transpare’nt spinel sintered body will be explained in detail hereinafter.
A1203 and MgO, or an aluminium compound and a magnesium compound which are respectively formed into A120. and M90 by calcination, are mixed in a molar ratio of A120M90 of from 0.50/0.50 to 50 0.525/0.475 in order to obtain a spinel sintered body having a given mixing ratio of Al,OM90. The resulting mixture is thoroughly mixed in a ball mill, and then calcined at 1,1 50-1,3000C in air for preferably at least one hour. The calcined mixture, after preferably being finely divided, is mixed with 0.01-0.2% by weight of LiF based on the amount of the calcined mixture to produce a raw material mixture. In order homogeneously to mix the calcined mixture with LiF, it is preferable that the calcined 55 mixture and LiF are mixed in a ball mill together with distilled water. The resulting raw material mixture is fully dried as such, and further fully dried together with a temporary bonding agent, such as polyvinyl alcohol, as a moulding aid. After the dried mixture is preferably made into uniform size by passing the mixture through a 60-mesh sieve (JIS standard), the mixture is moulded into a given shape.
The resulting moulded article is fired under a hydrogen atmosphere, a vacuum or an inert gas 60 atmosphere. The firing of the moulded article is effected by a two-stage firing. The primary firing of the moulded article is carried out by keeping the article at a constant temperature within a temperature range of 1,200-1,4001C or by gradually heating the article at a rate of temperature increase of about 501C/hr within the temperature range of 1,200-1,400’C, and the secondary firing of the primarily 2 GB 2 031 399 A 2 fired article is carried out by keeping the article at a constant temperature within a temperature range of 1,700-1,9001C or by gradually heating the article at a rate of temperature increase of not higher than 50112/hr within the temperature range of 1,700-1,9001C, wherein the rate of temperature increase within the temperature range between the primary step and the secondary firing step is not higher than 1 OOOC/hr, whereby a polycrystalline transparent spinel sintered body according to the present invention is produced. It is particularly important during the firing that the primarily fired article is fired gradually at a low rate of temperature increase of not higher than 1 OWC/hr within the temperature range between the primary firing step and the secondary firing step.
As the A1203 raw material and MgO raw material, either powdery A1,0, powdery MgO or an aluminium compound or a magnesium compound which respectively form A1,0, and MgO by thermal 10 decomposition, can be used. However, the use of an aluminium compound and a magnesium compound is preferable, because a uniform mixture of finely divided A1203 powder and MgO powder is formed. The transparent spine] sintered body of the present invention contains A1201 in a molar ratio higher than the molar ratio in the starting A120. and MgO powdery mixture for spinel due to the vapourization of M90 from the sintered body during the firing. The ratio of A1203 to M90 in the resulting sintered body varies 15 depending upon the composition of the starting A’203 and MgO powdery mixture for spinel, the firing temperature and the firing time. However, it is necessary that a spinel sintered body having a good transmissivity has a molar ratio of A120M90 within the range of 0.52/0.48- 0.70/0.30. when the molar ratio of Al201/M90 is higher than 70/30, a second phase consisting mainly of A1203 is apt to be precipitated at the grain boundaries, while when the molar ratio of A12031/M90 is lower than 0.52/0.48, 20 pores cannot be completely removed due to exaggerated grain growth. Therefore, a spinel sintered body having a molar ratio of A120./M90 higher than 0.70/0.30 or lower than 0.52/0.48 has a very poor light transmittance.
The reason why the amount of LiF contained in the sintered body is limited to 0.001-0.1 % by weight is as follows. When the amount of LiF is more than 0.1 % by weight, the above-mentioned second phase is precipitated at the grain boundaries of the spinel, while when the amount of LiF is less than 0.001 % by weight, pores cannot be completely removed, and a sintered body containing more than 0.1 % by weight or less than 0.001 % by weight of LiF has a poor light transmittance.
Further, the reason why the molar ratio of A1203 to MgO in the starting A1203 and MgO powdery mixture for spine] is limited within the range of from 0.50/0.50 to 0. 525/0.475 is that when the molar 30 ratio of Al20,/M90 exceeds 0.525/0.475, the above-mentioned second phase consisting mainly of excess A1203 is apt to be precipitated at the grain boundaries, and the light transmittance of the resulting sintered body decreases.
The reason why the starting Al;,Q3 and Mg.0 powdery mixture is calcined at 1,1 50-1,3000C is as follows’When the calcination temperature is lower than 1,1 501C, A1203 does not sufficiently react with 35 MgO, and spine] powders having non-uniform ratios of A120^0 are apt to be formed, while when the calcination temperature is higher than 1,3000C, exaggerated grain growth occurs and uniform grain growth in the following firing step is disturbed.
The reason why the calcined mixture of A1203 and MgO is mixed with 0.01 0.2% by weight of LiF based on the amount of the mixture is as follows. When the amount of LiF is larger than 0.2%, more than 0.1 % by weight of LiF remains in the resulting sintered body, and the above-mentioned second phase is precipitated to decrease the light transmittance of the sintered body, while when the amount of LiF is smaller than 0.01 % by weight, the amount of LiF remaining in the sintered body decreases to less than 0.001 % by weight, and the effect of the LiF does not occur and a transparent spinel sintered body cannot be obtained.
The reason why the firing atmosphere is limited to a hydrogen atmosphere, a vacuum or an inert gas atmosphere is that a transparent spinel sintered body cannot be obtained when these atmospheres are not used..
The reasqnwhy the primary firing is carried out at a temperature of 1,2001,4000C is that a primary firing temperature lower than 1,2000C is too low to form a dense sintered body, while a 50 primary firing temperature higher than 1,4001C causes exaggerated grain growth in the following firing steps. The reason why the rate of temperature increase for the primarily fired article within the temperature range between the primary firing step and the secondary firing step is limited to not higher than 1 001G/hr is that a rate of temperature increase of higher than 1 OOOC/hr causes rapid local grain growth, and pores are apt to be closed in the article, and hence the light transmittance of the 55 resulting sintefed body is lowered.._ Further, the reason why the secondary firing temperature is limited to 1, 700-1,9000C is that, when the firing tem’perature is lowerthan 1,7000C, a spinel sintered body having an excellent transmissivity cannot be obtained, while when the firing temperature is higherthan 1,9001C, exaggerated grain growth occurs and cracks are formed in the grain boundaries.
The invention will be further described with reference to the following illustrative Example.
EXAMPLE
Guaranteed reagents of ammonium alum and magnesium nitrate were mixed in amounts such that the resulting mixture contained A1,0, and MgO in a molar ratio as shown in the following Table 1, 65 j 04 3 GB 2 031 399 A 3 and the resulting mixture was calcined in air at 1,200’C for 3 hours. It was found from X-ray diffractometry that the calcined powder had an X-ray diffraction pattern of spinel, and the powder had a grain size of not larger than 1 pm. The calcined powder was mixed with LiF in an amount as shown in Table 1 based on the amount of the calcined powder, and the resulting mixture was mixed in a wet state for 3 hours together with plastics balls. Then, the above treated mixture was heated at 50WC for 1 hour 5 in air to remove the plastics residue, mixed with 2% by weight of PVA and dried. Then, the mixture was passed through a 60-mesh sieve QIS standard) to be made into uniform grain size. The powders were preliminarily moulded in a mould and then subjected to a pressure of 2, 500 kg/cM2 in an isostatic press. The resulting shaped articles was heated at 7001C for 3 hours in air to remove the binder. Then, under an atmosphere as shown in Table 1, the above treated shaped article was subjected to a primary firing 10 at 1,3000C for 3 hours and further to a secondary firing under a temperature and time condition as shown in Table 1. Between the primary and secondary firing steps, the primarily fired article was heated from 1,3000C to 1,7000C at a rate of temperature increase as shown in Table 1.
For comparison, sintered bodies were produced under the same conditions as described above, except that the molar ratio of A1,0,/MgO in the starting A1,0, and MgO powdery mixture for spinel, the 15 addition amount of LiF to the calcined mixture of A120, and MgO, and/or the rate of temperature increase between the primary and secondary firing steps were outside the range defined in the method of the present invention.
The spinel sintered bodies produced by the method of the present invention were compared with the comparative spinel sintered bodies with respect to the molar ratio of A’203to M90, the LiF content 20 and the in-line transmission in a thickness of 1.5 mm and at a wave length of 0.6 pm. The obtained results are shown in Table 1.
P.
Table 1(a)
Maximum firing Composition of temperature starting A120 Addition and time Temperature and MgO poWery amount raising rate Composition of LIF In-line mixture for spinel of LiF Tempera- between sintered body content transSample (molar ratio) (% b ‘ y Atmo- ture Time 1,300-1 7000C (molar ratio) (% b mission No. Aú203: M90 weight) sphere (0 C) (hr) (C/9r) A1203: M90 weigL) (%) 1 9.501 0.499 0.05 H2 1,700 5 20 0.557 0.443 0.02 64.5 2 0.501 0.499 0.05 vacuum 1,800 5 50 0.603 0.397 0.010 67.1 3 0.501 0.499 0.110 vacuum 1,800 5 50 0.596 0.404 0.022 67.5 4 0.501 0.499 0.20 H2 1,700 1 50 0.527 0.473 0.100 60.1, 0.501: 0.499 0.20 vacuum 1,800 5 100 0.583: 0.417 0.041 61.3 6 0.505 0.495 0.01 He 1,700 10 20 0.573 0.427 0.004 62.8 7 0.505 0.495 0.01 H2 1,850 10 20 0.646 0.354 0.001 69.0 8 0.505 0.495 0.01 He 1,800 3 50 0.575 0.425 0.004 64.0 Sintered 9 0.505: 0.495 0.110 He 1,800 3 100 0.570: 0.430 0.034 60.5 body pro- 10 0.505: 0.495 0.10 H2 1,800 3 50 0.576 ‘ 0.424 0.031 68.8 duced by 11 0.505: 0.495 0.20 H2 1,850 10 100 0.641: 0.359 0.030 64.5 the 12 0.512 0.488 0.05 H2 1,800 10 50 0.618 0.382 0.012 72.3 method 13 0.512 0.488 0.05 Ar 1,850 5 50 0.628 0.372 0.011 60.7 of the 14 0.512 0.488 0.15 Ar 1,750 10 50 0.597 0.403 0.053 62.5 present 15 0.512: 0.488 0.15 vacuum 1,750 10 100 0.607: 0.393 0.038 61.0 inven- 16 0.512 0.488 0.20 vacuum 1,700 5 20 0.573 0.427 0.081 64.8 tion 17 0.525 0.475 0.10 H2 1,700 5 20 0.579 0.421 0.048 65.1 18 0.525 0.475 0.110 H2 1,850 15 50 0.697 0.303 0.010 60.5 19 0.525 0.475 0.1.5 vacuum 1,800 10 50 0.637 0.363 0.021 63.8 0.525 0.475 0.20 He 1,800 10 50 0.623 0.377 0.055 63.1, 21 0.525 ‘- 0.475 0.20 1712 1,800 10 100 0.629: 0.371 0.045 1 66.5 0 G) m N) 0 W W CD (D -P.
b m 1 Table 1(b)
Maximum firing Composition of temperature starting M203 Addition and.time Temperature and MgO powdery amount raising rate Composition of LiF In-line mixture for spine] of LiF Tempera- between sintered body content transSample (molar ratio) (% by Atmo- ture Time 1,300-1,700C (molar ratio) (% by mission No. Aú203: M90 weight) sphere (- C) (hr) 1 (C/hr) A1203: M90 weight) (%) 22 0.463 0.537 0.40 H2 1,650 5 50 0.486 0.514 0.220 41.3 23 0.463 0.537 0.40 Ar 1,750 10 150 0.547 0.453 0.140 39.5 24 0.463 0.537 0.10 Ar 1,750 10 150 0.551 0.449 0.035 41.6 0.480 0.520 0.30 vacuum 1,600 15 50 0.501 0.499 0.140 47.2 Compara- 26 0.480 0.520 0.30 CO 1,800 5 50 0.565 0.435 0.098 38.1 tive 27 0.480: 0.520 0.20 CO 1,800 5 1Q0 0.559: 0.441 0.065 35.7 sintered 28 0.533 0.467 0.10 H2 1,750 10 200 0.618 0.382 0.030 48.9 body 29 0.533 0.467 0.10 H2 1,850 5 200 0.652 0.348 0.021 45.6 0.533: 0.467 0.35 H2 1,850 5 100 0.659: 0.341 0.063 44.3 31 0.551 0.449 0.15 vacuum 1,600 10 50 0.579 0.421 0.071 42.1 32 0.551 0.449 0.40 H2 1,800 10 50 0.655 0.345 0.100 44.7 33 0.551 0.449 0.1,0 H2 1,800 10 150 0.650 0.350 0.026 42.3 1 i i 1 1 1 m cj N 0 A? W (D m 1 (71 6 GB 2 031 399 A 6 It can be seen from Table 1 that all the spinel sintered bodies produced by the method of the present invention have an in-line transmission of higher than 60% and an excellent light transmission, but the comparative spinel sintered bodies produced under conditions outside the scope of the method of the present invention have a very poor in-line transmission.
The polycrystalline transparent spinel sintered bodies produced by the method according to the invention have an excellent light transmission due to the synergistic effect of the combination of the specifically limited mixing ratio of A1203 to MgO, the amount of A1203 being larger than the stoichiometric amount of A1203 for spinel, the specifically limited addition amount of Lif and the rate of temperature increase of not higher than 1001 C/hr within the specifically limited temperature range, the10 optical defects lowering the light transmittance of conventional polycrystalline spine[ sintered bodies being thus overcome. The sintered bodies produced by the method according to the invention are particularly useful as materials for discharge lamps and other optical materials, such as windows for transmitting infrared rays and windows for watches.

Claims (5)

1. A polycrystalline transparent spinel sintered body consisting mainly of A1203 and MgO’n a molar ratio of A1203/M90 of from 0.52/0.48 to 0.70/0. 30, and containing 0.001-0.1% by weight of UR

2. A polycrystalline transparent spinel sintered body as claimed in Claim 1, having an in-line transmission of higher than 60%.

3. A polycrystalline transparent spinel sintered body according to Claim 1, as described in any of sample nos. 1 to 21, 24 and 26 to 33 of the foregoing Example.

4. A method of producing a polycrystalline transparent spinel sintered body, comprising mixing A1203 with MgO, or mixing an aluminium compound with a magnesium compound which are respectively formed into A120. and MgO by calcination, in a molar ratio of A120YM90 of from 0.50/0.50 25 to 0.525/0.475, calcining the mixture at 1,1 50-1,3001C, mixing the calcined mixture with 0.01-0.2% by weight of LiF based on the amount of the calcined mixture, moulding the resulting mixture into a given shape, and subjecting the resulting shaped article to a primary firing at 1,200-1,4001C and then to a secondary firing at 1,700-1,9001C under a hydrogen atmosphere, a vacuum or an inert gas atmosphere, wherein the rate of temperature increase is not higher than 1 001C/hr within the temperature range between the primary firing step and the second firing step.

5. A method according to Claim 4 of producing a polycrystalline transparent spinel sintered body, substantially as herein described in any of Sample nos. 1 to 21 of the foregoing Example.
Printed for Her Majesty’s Stationery Office by the Courier Press, Leamington Spa, 1980. Published by the Patent Office. 25 Southampton Buildings, London. WC2A 1 AY, from which copies may be obtained.
5_ 1 1 1 1

GB7927727A
1978-08-14
1979-08-09
Polycrystalline transparent spinel sintered body

Expired

GB2031399B
(en)

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JPS5527837A
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1978-08-14
1978-08-14
Polycrystal transparent spinel sintered article and its manufacture

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1982-08-11

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Polycrystalline transparent spinel sintered body

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US4273587A
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Ｊｘ金属株式会社
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High-aluminum-content magnesia-alumina spinel transparent ceramic powder and preparation method thereof

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Method for sintering magnesia-alumina spinel transparent ceramic in inert atmosphere

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Robert Bosch Gmbh, 7000 Stuttgart

Ignition distributor for internal combustion engines with control generator

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1971-08-03
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1973-10-09

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1972-07-24
1974-09-10
Gte Sylvania Inc
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1972-08-25
1973-10-30
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Method for making heat resistant transparent optical elements

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(en)

1973-07-03
1976-07-21
Nikex Nehezipari Kulkere
Process for the manufacture of translucent polycrystalline alumina bodies

US3950504A
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1974-09-26
1976-04-13
Quigley Company, Inc.
Process for producing magnesium aluminate spinel

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1976-09-30
Предприятие П/Я А-3944

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1978-08-14
JP
JP9894778A
patent/JPS5527837A/en
active
Granted

1979

1979-08-08
US
US06/064,841
patent/US4273587A/en
not_active
Expired – Lifetime

1979-08-09
GB
GB7927727A
patent/GB2031399B/en
not_active
Expired

1979-08-13
DE
DE2932789A
patent/DE2932789C2/en
not_active
Expired

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DE3319346A1
(en)

1982-12-27
1984-06-28
NGK Insulators Ltd., Nagoya, Aichi

POLYCRYSTALLINE TRANSPARENT SPINNEL SINTER BODY AND METHOD FOR THE PRODUCTION THEREOF

US4769352A
(en)

1984-07-23
1988-09-06
Norton Company
Refractory cement containing lithium fluoride flux

US4735925A
(en)

1985-06-14
1988-04-05
Ngk Spark Plug Co., Ltd.
Low-temperature sinterable ceramic composition

EP0332393A1
(en)

1988-03-09
1989-09-13
Sumitomo Electric Industries, Ltd.
Method of producing a light-transmitting spinel sintered body

US5152940A
(en)

1988-03-09
1992-10-06
Sumitomo Electric Industries, Ltd.
Method of producing a light-transmitting spinel sintered body

EP1873129A1
(en)

2005-03-30
2008-01-02
Sumitomo Electric Industries, Ltd.
Spinel sintered body, light transmission window and light transmission lens

EP1873129A4
(en)

2005-03-30
2011-04-13
Sumitomo Electric Industries
Spinel sintered body, light transmission window and light transmission lens

US8097550B2
(en)

2005-03-30
2012-01-17
Sumitomo Electric Industries, Ltd.
Spinel sintered body, light transmitting window and light transmitting lens

WO2008074503A1
(en)

2006-12-21
2008-06-26
Carl Zeiss Smt Ag
Transmitting optical element

US8163667B2
(en)

2006-12-21
2012-04-24
Carl Zeiss Smt Gmbh
Transmitting optical element with low foreign-element contamination

US9624136B2
(en)

2014-07-01
2017-04-18
Corning Incorporated
Transparent spinel article and tape cast methods for making

Also Published As

Publication number
Publication date

GB2031399B
(en)

1982-08-11

US4273587A
(en)

1981-06-16

DE2932789A1
(en)

1980-03-06

DE2932789C2
(en)

1982-07-15

JPS5527837A
(en)

1980-02-28

JPS5727055B2
(en)

1982-06-08

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