JP2008514532A - Method for producing glass ceramic composite molded body and composite molded body - Google Patents

Abstract

【Task】
The present invention relates to a method for manufacturing a glass-ceramic composite molded body, and more particularly to a method for manufacturing at least two glass-like constituent pieces, ie, glass-like cast bodies, by bonding, in particular by adhesion. The glassy components are arranged in an overlapping manner in the joining region, where the contact surfaces to be bonded are in contact and are heated to a temperature T2 above the glass transition temperature Tg in the crystal nucleation stage, at which the crystals Nuclei are precipitated and then crystallized by heat treatment in the nucleation stage. The glassy piece to be bonded and the optimally pre-nucleated piece are bonded to each other depending on the material in the crystallization temperature range during the viscous flow, forming a diffusion composite in the area of the joining surface Is done.
[Selection] Figure 4

Description

  The present invention specifically relates to a method for producing a glass-ceramic composite molded body having the features described in the superordinate concept of claim 1, and a composite molded body, particularly a hermetic or high-pressure hermetic composite molded body.

  Many types of glass-ceramic composite compacts are known from the prior art in terms of their construction and geometry, which are different from one another. These molded bodies are formed by an adhesion process, particularly by a low temperature welding method. However, the method requires that the surface quality of the pieces to be joined together is high and that certain temperature heating rate relationships are accurately observed. In this case, only chemically compatible materials can be joined. A bond with high load capacity and no residual stress is obtained only if the thermal expansion coefficients of the materials to be joined are approximately equal. The acceptable range is usually less than 0.2 ppm / K. Further, the low temperature welding is usually performed at a temperature range in which the holding time is increased to, for example, 1 hour and the glass or glass ceramic behaves viscoelastically, that is, the viscosity log η / dPas is 10 or more. This type of method is characterized by long process time and high power consumption. However, the metal diffusion welding process is performed at a pressure of 0.6 to 0.8 times the melting point, that is, simultaneously when the materials to be joined are in the solid phase. In Patent Document 1, this applies to the inorganic crystal material in substantially the same manner.

  Patent Document 2 discloses a method of directly bonding and crystallizing glass. In this case, only materials with the same chemical composition are bonded together. It is essential in this case that the surface quality of the materials bonded together is high. In order to perform with a lower surface quality, an additional heat treatment must be performed, in which the annealing process is performed up to the glass transition temperature Tg.

  From Patent Document 3, thermal bonding of lithium disilicate glass ceramic to ferrite is known. This material is a material having a high coefficient of thermal expansion such as CTE> 11 ppm / K.

  Patent Documents 4 to 6 describe other methods for bonding a crystallizable glass to form a glass ceramic molded body. They disclose a useful method for bonding glassy components, particularly disk-like glassy components between one another. In the case of the method described in Patent Document 4, two disk-shaped elements made of glass ceramic raw glass are overlapped with each other, and an intermediate layer made of the same material is intermediately bonded. Further, the glass is heated and held to a temperature at which the viscosity log η / dPas of 7 to 9 is generated, thereby causing diffusion bonding. The bonds thus formed are subsequently cooled to an optimum nucleation temperature, maintained at that temperature for a certain period of time, and further heated to a higher temperature for crystallization.

  On the other hand, Patent Document 6 describes a method in which a disk-like object made of glass ceramic raw glass having the same chemical configuration is bonded to obtain a bonded glassy composite. There, it is first heated to a glass transition temperature Tg and then to a temperature at which the viscosity log η / dPas becomes 7 to 9 at a heating rate of 10 K / min or more. At this time, bonding is performed. In the cooling stage following this heating, the temperature is such that the viscosity log η / dPas is 10, and this cooling is performed at a speed at which crystallization is completely avoided.

  According to Patent Document 5, the following method is known as an adhesion method for glassy constituent pieces. That is, this bonding is performed for a very long time at a temperature at which the glass has a viscosity of log η / dPas of 10 to 14 and at the same time at which nucleation is performed, and crystal precipitation is performed at a high temperature following this nucleation. It is the method characterized by this.

  U.S. Pat. No. 6,057,031 discloses two methods of manufacturing lightweight mirror supports from glass or glass ceramic, which are done by bonding individual pieces in the form of glassy components. These individual pieces are hollow bodies, each having an opening on at least one of its front faces, and bonding the side surfaces of these hollow bodies to each other. For this purpose, the first method is to use a single composite of individual glassy components as follows: the glass begins to flow plastically and is bonded to each adjacent glassy component. Is heated to a temperature at which it does not crystallize. Crystallization takes place in subsequent stages, where the entire glassy composite is heated to a temperature at which crystal nucleus precipitation and crystallization occur. In the second method, the glassy component pieces are first individually ceramicized. These glass ceramic pieces are then heated to a temperature at which they each bond with adjacent component pieces.

  As the ceramization process, the one similar to the principle of the first method described in Patent Document 7 is used for manufacturing a glass ceramic composite composed of a bundle of thin glass tubes having a hexagonal channel cross section (patent). Document 8). In this case, melting of the glass ceramic is performed simultaneously with crystal nucleation at a temperature higher than the annealing temperature OKP. This temperature is a temperature at which the log has a log η / dPas of 13, more precisely a temperature between [OKP + 28K] and [OKP + 140K]. The resulting joint is heated at a rate of at least 0.47 K / min from [OKP + 110K] to [OKP + 140K] or higher, at which time crystallization occurs. In this case, the glassy component is heated at a suitable rate that does not cause unacceptably significant temperature changes to a temperature in a range that maximizes glass crystal formation. During this heating, melting and crystal formation occur. Crystallization takes place at any temperature in the temperature range above the crystal nucleation-lattice expansion-melting temperature and above the upper critical devitrification temperature Ti. Melting occurs in this case with crystallization due to deformation of the individual glassy constituent pieces. The premise here is that the rate of temperature increase during ceramization is not excessively slowed in order to cause noticeable deformation. The disadvantage of this method is that it does not provide a constant shape compared to the starting material, which is unacceptable for many applications, especially if you want to produce a molded part, It is unacceptable if constrained to the mounting dimensions of the application currently selected.

The methods in the prior art are characterized by having different points of focus. These points of interest include bonding glass elements that have already been ceramicized, or combining individual components into a glassy composite and ceramicizing, for example during nucleation and crystallization. It is related to making the connection. Since these require a long holding time, they are very troublesome in terms of process time and process control, and require a lot of electric power.
US Pat. No. 5,846,683 European Patent Application No. 1375442 Japanese Patent No. 02064034 British Patent No. 11678895 British Patent No. 1167896 British Patent No. 1167897 US Pat. No. 3,514,275 German Patent Application No. 2119771

  It is therefore an object of the present invention to provide a method for bonding molded parts made of glass, in particular glass ceramic raw glass or blue glass, without using additional materials, depending on the material. This method also overcomes the above-mentioned drawbacks of the prior art, and in particular, the shape of each component piece joined together sufficiently matches the starting shape after joining, significantly reducing the process time and reducing energy consumption. What is done is desirable.

  The means for solving the above-mentioned problems in the present invention has the features described in claim 1. Preferred embodiments are described in the dependent claims. The glass-ceramic composite molded body produced according to the present invention has the characteristics described in claim 18.

  A method for producing a glass-ceramic composite molded body, i.e., a glass-shaped molded body, from at least two glass-like constituent pieces by joining, in particular by adhesion, the glass-like constituent pieces overlapping each other in the joining region, The joint surfaces to be joined are in contact with each other. Further, in the nucleation stage, crystallization occurs by heating to a temperature above the glass transition temperature Tg, that is, a temperature T2 at which crystal nuclei are precipitated, followed by heat treatment in the crystallization stage. The glassy components to be joined are optimally pre-nucleated and their joining areas are bonded together depending on the material. At this time, since the viscous flow is dominant in the crystallization stage, a diffusion bond is formed.

  Therefore, the present invention intentionally utilizes any process necessary for ceramification anyway, and at the same time, the process parameters set here also determine the properties of the joint. Further, additional processing steps in the prior art, that is, additional processing steps such as reheating can be omitted. Thereby, the process time can be remarkably shortened. Therefore, one heating curve is set at the end of the nucleation stage or at the start of crystal precipitation in the crystallization stage. The rate of increase or temperature ramp of this curve is selected depending on the desired time course of the viscosity reduction of the materials to be joined and the degree of reduction. In this case, the rate of increase of the heating curve is preferably 1 K / min or more, more preferably 5 K / min or more, and particularly preferably 7.5 K / min or more.

  In the solution according to the present invention, when a molded part made of glass ceramic raw glass or blue glass is produced in a fixed bond, the viscous flow of the glassy material optimally pre-nucleated is utilized. The above viscous flow is intentionally applied during the transition, i.e. in the crystallization temperature range, in order to effect a bond, in particular a bond depending on the material. By applying a heating curve to the crystallization temperature range leading to the nucleation region, nucleation disappearance is reduced. The steep heating curve further helps to quickly compensate for viscosity increases in the crystallization temperature range. This compensation is performed by crystal precipitation and growth, as well as chemical changes in the residual glass phase. In order to weld the planar regions where the pieces to be joined contact each other, or to form a diffusive bond between the planes, the viscous flow may be continued for several more minutes. Since the state of pre-nucleation is optimal, optimal crystallization is performed in terms of the content of the crystal phase, the size of the crystal, and the characteristics (for example, thermal expansion and transparency) resulting therefrom. Furthermore, since the viscosity between adhesions is small compared with the conventional method, the requirements for the quality of the surfaces to be joined are reduced. Therefore, the surface quality at the time of tip heat processing, pressing, or rolling can be made sufficient.

  The connection according to the present invention has a uniform shape by the above-described steps. In other words, the shape of the glass-like constituent piece sufficiently matches the shape or geometry at the start even after being combined into a composite molded body by ceramization.

  Bonds depending on the material are in this case preferably produced without any additional pressure from any pressure source, unlike conventional diffusion bonds. As a result, there is no effect on the shape of the component piece. However, it is particularly advantageous that the pressure due to the weight of the component pieces can be used to fix the connection. For this purpose, the glass-like components are placed one on top of the other in the vertical direction at the start. In this case, it is preferable to place the component with the greater weight on the top.

  The bond according to the material between the glassy components to be joined together is formed without using an adhesive. As a result, the properties of the bonding zone are not affected by different materials.

  In the process according to the invention, in particular lithium-aluminum-silicate type glass ceramic (so-called LAS-glass ceramic), magnesium / zinc-aluminum-silicate type (so-called MAS- or ZAS-glass ceramic), or each of these Mixtures of systems can be used for the raw glass. In this case, the expansion coefficient of the resulting glass ceramic should not exceed 8 ppm / K at 30 to 300 ° C. If it exceeds this, a very high stress is generated on the joint surface while it is cooled to room temperature, and the bond may be broken by this stress. It has also been observed that in other methods according to the invention, a glass-ceramic bond is obtained, which comprises an aluminum silicate type glass or amorphous silicon dioxide (so-called quartz glass).

  Heating in the nucleation stage is performed until the temperature reaches T2. It has a viscosity log η / dPas of more than 10, preferably more than 10 to 14. This temperature allows optimal nucleation. The holding time is several minutes to several hours depending on the chemical composition of the raw glass and the properties desired for the glass ceramic, but is preferably 15 minutes to 60 minutes.

By the method of the present invention, it becomes possible to produce a complexly molded glass ceramic composite molded body. In this case, the underlying glassy component is
They differ from each other in terms of their glass composition and / or geometry. A particularly advantageous application of this method is in the case of producing an airtight or high pressure sealable composite molded body. This composite molded body is formed of a first glass-like constituent piece that is a hollow body that is open on one side and a second glass-like constituent piece. The latter is used for sealing the opening of the hollow body with air tightness and high pressure tightness. At that time, a glass ceramic composite molded body having a shape of a composite hollow body is formed.

  However, in a particularly preferred embodiment, each glassy component has a matching viscosity / temperature characteristic and / or a high degree of mutual penetration, and the viscosity of the generated glass ceramic is from log η / dPas of 8 Join in 10 regions.

  In order to obtain a bond that is low in stress and can withstand high loads, each glassy component is preferably joined with a coefficient of thermal expansion CTE of less than 8 ppm / K and a coefficient of thermal expansion that is as equal or approximately equal.

  In one particularly preferred application embodiment, the method of the invention is used not only for bonding the glassy component itself, but also for applications where at least one of the glassy component is additionally bonded to a metal element. it can. However, in this case, it is preferable to use a metal element having a small difference even if the thermal expansion coefficient is equal to or different from that of each glass-like component piece.

  The solving means in the present invention will be described below with reference to the drawings.

  FIG. 1 is a simplified schematic diagram of the basic steps of the method according to the invention, showing the production of a glass-ceramic composite body 1 from at least two glass-like components 2 and 3 that are joined together. These constituent pieces are glass-like molded parts, in particular those parts made of glass ceramic raw glass or blue glass. These molded parts can be in any form in terms of their geometry and the construction of the raw glass. Bonding is performed by bonding according to the material. Each of the glass-like constituent pieces 2 and 3 has at least one plane region, and this plane region functions as the joining surfaces 4 and 5, and bonding according to the material is performed through this plane region. Thereby, both glass-like component pieces 2 and 3 are arranged to overlap each other in the joining region 6. That is, the joint surfaces 4 and 5 are in contact with each other. In this case, the bonding region 6 is a region where both the glass-like components 2 and 3 are directly bonded according to the material after bonding. The glassy structural pieces 2 and 3 are first crystal nucleated in advance at the nucleation stage. Therefore, these components are heated from the starting temperature T1 to the temperature T2. The latter temperature is higher than the glass transition temperature Tg and is a temperature at which crystal nuclei are precipitated. This temperature T2 corresponds to a viscosity of log η / dPas of more than 10, preferably more than 10 and not more than 14. The glass is held at this temperature T2 for a time t in order to precipitate crystal nuclei. This time preferably refers to the time at which the precipitation of nuclei is maximized, but is a short time for diffusion bonding to occur between the planar regions 4 and 5 where the glassy components 2 and 3 are in contact with each other. In this case, the holding time is usually several minutes to several hours, preferably 15 to 60 minutes, depending on the components of the glass ceramic. The glassy components 2 and 3 that are optimally pre-nucleated in this way are then heated according to a heating curve for crystallization with a very steep crystallization peak region. As a result, the increase in viscosity in the crystallization temperature range is compensated in a short time, and as a result, the time during which the viscous flow can be used is lengthened. As a result, the joining surfaces 4 and 5 that are in contact with each other while overlapping each other are fused in a substantially fluid state, and an integral composite molded body 1 can be formed by diffusion bonding. In this case, the viscosity of the glass can be varied as a function of the slope or rate of increase of the heating curve within a certain range of the crystallization temperature range leading to the nucleation region. This is to maintain the shape of the glass-like component pieces 2 and 3 almost constant except for the joining region 6. The nucleation stage and the crystallization stage preferably follow each other, i.e. do not overlap or only slightly overlap.

  FIG. 2 shows a schematic curve 9 showing a generally known process for the relationship between the viscosity and temperature of the selected glass. The viscous behavior of glass or glass ceramic is generally defined when the viscosity log η / dPas is less than 10.2, that is, below the “dilatometry softening point (Ew)” shown in FIG. The accompanying temperature depends on the type of glass, and in the case of the illustrated glass type, it is approximately 820 ° C. or higher. For the known viscosity behavior of glass with respect to temperature, see Heinz G. et al. See Pfender, “Schott Guide to Glass, Chapmann S. Hall”, 1992, pages 20-23.

  FIG. 3 is a graph showing the thermodynamic process during the ceramic reaction of the glass ceramic. In this case, the basic structure of the glass ceramic shown in Table 1 of the present specification is assumed.

Described in the figure is a viscous resistance η in units of dPas at a temperature T in units of ° C. Here, an example of a heating rate of 5 K / min is shown. A DTA graph 100 is assigned to this heating rate, which reproduces heat absorption and heat release by the sample. In the temperature / viscosity resistance graph, a gray portion indicates a region A of the viscous flow that is used for adhesion while focusing on the target. Exothermic crystal precipitation is represented by a steep increase in the DTA curve 100, and it can be seen that a clear decrease in viscosity 110 occurs as the heat of crystallization is released as the crystal precipitation begins. In this case, a decrease corresponding to half the first power of 10 occurs from 10 ^9.5 to 10 ⁹ Pas. As a result of the formation of crystallites, the tissue structure is fixed and the viscosity rises again. In the example shown, the rise is within 3 minutes. The minimum viscosity 120 at the start of the crystallization stage can be intentionally determined or adjusted by the slope of the heating curve. In general, in this case, the viscosity or viscous resistance decreases as the heating rate increases. If the heating curve is steep, the increase in viscosity due to the progress of crystallization moves to a higher temperature. In addition, the viscous flow state may be used for a longer period of time in order to create a bond between the two components to be joined. Not only the quality and size of the bond, but also the shape stability with respect to the starting shape is determined by the time of joining and the heating rate.

  In a particularly preferred embodiment of the method according to the invention, additional pressurization is omitted by an external pressure source. It is also possible to use the pressure resulting from the weight of the component pieces acting on the planar area to be joined. Therefore, the component pieces 2 and 3 are placed at the positions shown in FIG. That is, at least a part is vertically stacked in the vertical direction. This has the advantage that the shape stability of the joint is not adversely affected.

  FIG. 4 is a simple schematic diagram showing a case where the method according to the present invention is applied to the production of the glass ceramic composite molded body 1. This molded body is an integrated glass ceramic composite hollow body 7 having airtightness and high-pressure sealing performance. This composite hollow body comprises a first glass-like component 2 that takes the form of a glass cap 8, which forms a hollow space 9. In this invention, the opening part 11 which the hollow space 9 forms is closed using the flat glass plate or glass disk 10 which is the 2nd glass-like structural piece 3, Thereby, this hollow space can be closed. . This bond is obtained by diffusion bonding at the joint surfaces 5 and 6. The joining surface 5 includes an opening 11 on the front surface 12 of the glass cap 8 and is preferably formed in a ring shape. The joining surface 6 is formed by a part of a plane, here a ring-shaped surface, preferably in the outer diameter region. By the thermal bonding performed by the method according to the present invention, the joining regions 6 of both the component pieces 2 and 3 are melted together to form the composite hollow body 7 while maintaining the shape of the other parts.

  One particularly preferred application of the method according to the invention is suitable for obtaining a composite hollow body 7, in which case the metal element 14 is applied to at least one of the component pieces 2 or 3, here to the component piece 3. Holes 13 can be provided. The attachment of the metal element 14 can be effected by geometric bonding, mechanical bonding, or bonding depending on the material. The metal element 14 is preferably a hollow body, in particular a hollow wire. Preferably, a metal element 14 having a thermal expansion coefficient equal to that of the glass ceramic raw glass, such as metal molybdenum, tungsten, or Kovar (KOVAR) alloy is used. While the glass is heat treated until crystallization begins, the glass and metal elements expand with approximately the same expansion coefficient. This is because, in a preferred embodiment of the present invention, the thermal expansion coefficient of a glass ceramic raw glass component, for example, blue glass, is almost the same as the thermal expansion coefficient of the metal. When the blue glass is ceramized, the glass ceramic shrinks on the metal element 14 as crystallization shrinkage of about 2% occurs during crystallization. In the subsequent cooling step, the hermeticity of the connection between the metal element 14 and the composite hollow body 7 is maintained by the shape connection or the mechanical connection. At this time, one stress state is generated, and this stress state can be expressed as a function of the material composition ratio between the glass ceramic and the metal element 14.

  In a particular aspect of the preferred embodiment described above, the metal element is subjected to penetration by a viscous liquid glass material or glass ceramic material during crystallization. In this way, a shape bond, a mechanical bond, and a bond corresponding to the material having airtightness by fusion welding are formed between the glass ceramic and the metal element 14.

  In a particularly preferred embodiment, the metal element is bonded to the glass-like component 3 in a state of being airtight and infiltrated by bonding depending on the material, prior to ceramization. Bonding depending on this material is maintained during the ceramization process, and the tightness of the bond is further improved by strengthening the geometric and mechanical bonding process with ceramization shrinkage.

  In other embodiments, soldering can be applied between the metal element 14 and the hole 13 as an intermediate element. For example, a ring made of a pre-formed glass frit is used. The glass frit melts during the heat treatment, penetrates the metal element 14 and the composite hollow body 7, and bonds them together in an airtight state. Preferably, this method is applied when the thermal expansion coefficients of the glass ceramic and the metal element 14 differ by 4 ppm / K or more.

  Examples of the present invention will be described below. Table 1 shows the configuration of the glass ceramic raw glass used in Examples 1 to 6 in Table 2.

  This relates to lithium-aluminum-silicate glass.

  Not only the composition of each glass but also the thermal expansion coefficient of blue glass is described. In the region of 3 to 5 ppm / K, this thermal expansion coefficient is substantially the same as, for example, the thermal expansion coefficient of 4.8 to 5 ppm / K of molybdenum (Mo) or 4.5 ppm / K of tungsten (W).

  In the case of the first embodiment described in Table 2, the planar component piece I is formed from glass having a glass configuration GK1, and the roll-shaped component piece II is formed from glass having a glass configuration GK2.

Both glasses are held at a nucleation temperature of 750 ° C. for 30 minutes, starting from this temperature at a heating rate of 15 K / min to a temperature T 2 of 890 ° C., and crystallized at the latter temperature for 35 minutes. Thus, the high-pressure sealing property was larger than 1.5 bar, and the vacuum tightness was 3 · 10 ⁻¹⁰ mbar · l · s ⁻¹ .

  In the case of Example 2 in Table 1, the same material as that of Example 1 is selected as the material for the plane and the roll. However, unlike Example 1, crystallization is performed at 890 ° C. for 60 minutes.

  In the case of Example 3, the glass configuration of the second component piece is different. The second component piece had a glass configuration GK3, and the same process parameters as in Example 1 were selected.

  Example 4 differs from Example 3 in that the crystallization time is as short as 35 minutes at 890 ° C.

In Examples 5 and 6, the same material is used for the component I and the component II. The difference is the size of the main contact surface, the contact surface is 32.5 mm ² at 44.8 mm ^2, Example 6 In Example 5.

  The glass composition described in Table 1 is that used in Examples 1 to 6 in Table 2. In this case, ceramization was performed in the viscous flow region of the present invention. As described in FIG. 3, this viscous flow was in the region of 790 to 820 ° C. for the selected raw glass configuration.

  The joint produced by the method of the present invention was excellent in high-pressure sealing and airtightness against vacuum. The stress between the constituent pieces was sufficiently small, less than 20 MPa. The obtained composite molded body was very stable.

The schematic diagram which shows the process of the method which concerns on this invention. The graph which shows the relationship between the viscosity of general glass, and temperature. The graph which shows the thermodynamic process in the ceramization reaction. The schematic diagram which shows manufacture of the composite hollow body which applied the method by this invention.

Explanation of symbols

DESCRIPTION OF SYMBOLS 1 Glass ceramic composite molded body 2 Glass-like component piece 3 Glass-like component piece 4 Joining surface 5 Joining surface 6 Joining area 7 Composite hollow body 8 Glass cap 9 Hollow space 10 Glass plate or glass disk 11 Opening part 12 Front surface 13 Hole 14 Metal element

Claims (17)

  A method for producing a glass-ceramic composite molded body (1, 7) by joining, in particular adhering, at least two glass-like constituent pieces (2, 3), wherein the glass-like constituent pieces (2, 3) are In the bonding region (6), the bonding surfaces (4, 5) are arranged in contact with each other by a method of overlapping, and in the crystal nucleation stage, heated to a temperature T2 higher than the glass transition temperature Tg, which is a temperature at which the crystal nuclei are precipitated. The glassy components (2, 3) that are then crystallized by heat treatment in the crystallization stage and bonded together are in the region of their interface (4, 5) during viscous flow conditions in the crystallization temperature range. A method of forming a bond depending on the material.   Due to the end of the crystal nucleation phase or the start of crystal separation, a temperature gradient is set in the crystallization phase, due to an increase in that gradient over the desired time course and a decrease in the viscosity of the components (2, 3) to be joined. The method of claim 1, wherein the intensity continues.   3. The method according to claim 2, wherein the increase in temperature gradient is> 1 K / min, preferably> 5 K / min, particularly preferably> 7.5 K / min.   The method according to claim 1, wherein the bonding depending on the material occurs without being affected by an externally generated pressure.   The glassy component pieces (2, 3) are arranged in a vertically overlapping manner in the vertical direction at the start position, where the glassy component pieces (2, 3) are subjected to gravity due to their large weight. 5. The method according to any one of claims 1 to 4, wherein the method is arranged from above in a direction to perform.   6. A method according to any one of the preceding claims, wherein a bond depending on the material between the glassy components (2, 3) joined together is formed without the use of an adhesive.   Heating in the crystal nucleation step is performed at the temperature T2, which corresponds to a viscosity log η / dPas> 10, preferably> 10 to 14 or less. The method described.   The method according to any one of claims 1 to 7, wherein the glassy constituent pieces (2, 3) having different compositions are joined to the raw glass.   9. A method according to any one of the preceding claims, wherein the glassy components (2, 3) are joined with matching viscosity-temperature characteristics.   10. The glassy component (2, 3) is joined in a region of log η / dPas of 8 or more and 10 or less due to high mutual permeability due to the viscosity of the glass ceramic produced. The method described in 1.   11. The method according to claim 1, wherein the glassy component pieces (2, 3) are joined with a thermal expansion of CTE <8 ppm / K.   12. A method according to any one of the preceding claims, wherein at least one glassy component (2, 3) is additionally joined depending on the material by means of a metal element (14).   13. A method according to any one of the preceding claims, wherein the metal element (14) exhibits a thermal expansion similar to an individual glassy component (2, 3).   14. A method according to any one of claims 1 to 13, wherein the glassy components (2, 3) are joined by different geometries.   The first glass-like component piece (2) having the form of a hollow molded body having one side opened is opened by the second component piece (3) in a state of being airtight or high-pressure sealed. 15. Method according to claims 1 to 14, wherein the part is closed when forming the glass-ceramic composite body (1) in the form of a composite hollow body (7).   A glass-ceramic composite molded body (1) produced from at least two glass-like components (2, 3) by the method according to any one of claims 1 to 15.   The glass ceramic composite molded body (1) according to claim 16, obtained as a composite hollow body (7) having airtightness or high-pressure sealing property.

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