CN115636664B - Glass-ceramic system ceramic substrate material with adjustable shrinkage and preparation method thereof - Google Patents
Glass-ceramic system ceramic substrate material with adjustable shrinkage and preparation method thereof Download PDFInfo
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- CN115636664B CN115636664B CN202211388841.5A CN202211388841A CN115636664B CN 115636664 B CN115636664 B CN 115636664B CN 202211388841 A CN202211388841 A CN 202211388841A CN 115636664 B CN115636664 B CN 115636664B
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Abstract
The invention provides a glass-ceramic system ceramic substrate material with adjustable shrinkage and a preparation method thereof, belonging to the field of electronic information functional materials. According to the invention, two CBS microcrystalline glasses with different components, different softening temperatures and different crystallization characteristics are adopted, so that the shrinkage behavior of the substrate in the sintering process can be regulated and controlled, and the sintering warping phenomenon of the substrate and LTCC series slurry is improved; mgO and La in glass ceramics 2 O 3 The composite use can play a role in synergism, promote crystallization in the sintering process, reduce the content of glass phase in a sintered system and effectively reduce dielectric loss; adopts CBS microcrystalline glass and CaSiO 3 The composite system can increase the flatness and matching property of the co-firing of the substrate material and the LTCC slurry through the skeleton effect of the ceramic in the matrix; caSiO (CaSiO) 3 The dielectric constant of the substrate can be effectively regulated and controlled.
Description
Technical Field
The invention relates to the field of electronic information functional materials, in particular to a glass-ceramic system ceramic substrate material with adjustable shrinkage rate and a preparation method thereof.
Background
The low temperature co-fired ceramics (LTCC) technology adopts ceramic powder to prepare slurry, a raw ceramic film is formed by tape casting, punching, filling through hole metal slurry and printing circuit patterns on each layer of raw ceramic film, then each layer of raw ceramic sheet is subjected to alignment lamination and hot pressing, finally the ceramic sheets are sintered into a whole at the temperature of 850-900 ℃ to form a multilayer ceramic circuit, and the multilayer ceramic circuit is a basic technology for realizing miniaturization, integration and high frequency of circuit modules.
And as one of the most important LTCC substrate materials applied to the field of high-frequency communication, calcium-boron-silicon (CaO-B) 2 O 3 -SiO 2 CBS) based glass ceramics have a range of excellent properties, such as: relatively low sintering temperature<900 deg.c), extremely low dielectric constant (epsilon) r <6.5 And dielectric loss (tan delta)<1×10 -3 ) Therefore, the material is one of the most important LTCC substrate materials, but has the defects of single material system, difficult realization of performance regulation and serialization, narrow microcrystallization process window and easy occurrence of warping and sintering mismatch when being co-fired with LTCC series slurry. And the glass-ceramic composite material is a two-phase composite material sintered by taking microcrystalline glass powder and crystalline ceramic powder as basic materials. The material has the advantages of certain performance regulation space, and the disadvantage of poor dielectric property due to the influence of the composition of glass phase and ceramic components.
Therefore, how to realize the controllable shrinkage rate of the glass-ceramic composite material and simultaneously make the glass-ceramic composite material have good dielectric properties is a technical problem to be solved in the field.
Disclosure of Invention
The invention aims to provide a glass-ceramic system ceramic substrate material with adjustable shrinkage and a preparation method thereof.
In order to achieve the above object, the present invention provides the following technical solutions:
the invention provides a glass-ceramic system ceramic substrate material with adjustable shrinkage, which is prepared from the following raw materials: caO-B 2 O 3 -SiO 2 Is glass ceramics A, caO-B 2 O 3 -SiO 2 Is glass-ceramic B, caSiO 3 Base ceramic powder, solvent, dispersant, plasticizer and resin;
the CaO-B is 2 O 3 -SiO 2 Is glass ceramics A, caO-B 2 O 3 -SiO 2 Glass ceramics B and CaSiO 3 The mass ratio of the base ceramic powder is (60-80): (10-30): (5-20);
preparation of the CaO-B 2 O 3 -SiO 2 The microcrystalline glass A comprises the following raw materials: caCO (CaCO) 3 、H 3 BO 3 、SiO 2 MgO and La 2 O 3 ；
Preparation of the CaO-B 2 O 3 -SiO 2 The microcrystalline glass B comprises the following raw materials: caCO (CaCO) 3 、H 3 BO 3 、SiO 2 And Al 2 O 3 。
Preferably, the CaSiO 3 The base ceramic powder is Ca 1-x Cu x SiO 3 And the x is more than or equal to 0 and less than or equal to 0.025.
Preferably, the CaSiO is prepared 3 The raw materials of the base ceramic powder comprise CaCO 3 、SiO 2 And CuO.
Preferably, the CaO-B is prepared 2 O 3 -SiO 2 CaCO in the raw material of glass ceramics A 3 、H 3 BO 3 、SiO 2 MgO and La 2 O 3 The mass ratio of (40-70): (15-30):(20～35)：(0.5～2)：(0.5～3)。
preferably, the CaO-B is prepared 2 O 3 -SiO 2 CaCO in the material of glass ceramics B 3 、H 3 BO 3 、SiO 2 And Al 2 O 3 The mass ratio of (15-30): (15-30): (20-40): (5-20).
Preferably, the CaO-B is 2 O 3 -SiO 2 Is glass ceramics A, caO-B 2 O 3 -SiO 2 Glass ceramics B and CaSiO 3 The base ceramic powder is sieved by a 500-mesh sieve.
Preferably, the solvent includes two or three of ethanol, acetone and xylene; the dispersing agent is one or two of castor oil and oleic acid; the plasticizer is dibutyl phthalate; the resin is polyvinyl butyral.
The invention provides a preparation method of a glass-ceramic system ceramic substrate material with adjustable shrinkage, which comprises the following steps:
(1) CaO-B 2 O 3 -SiO 2 Is glass ceramics A, caO-B 2 O 3 -SiO 2 Is glass-ceramic B, caSiO 3 Mixing the base ceramic powder, a solvent, a dispersing agent, a plasticizer and resin to obtain ceramic slurry;
(2) Casting the ceramic slurry obtained in the step (1) into a green ceramic tape, and then sequentially cutting, laminating and carrying out temperature isostatic pressing to obtain a green body of the glass-ceramic system ceramic substrate;
(3) And (3) sequentially discharging glue and sintering the green body of the glass-ceramic system ceramic substrate obtained in the step (2) to obtain the glass-ceramic system ceramic substrate material with adjustable shrinkage rate.
Preferably, the temperature of the adhesive discharging in the step (3) is 450-600 ℃.
Preferably, the sintering temperature in the step (3) is 800-950 ℃, and the sintering heat preservation time is 10-30 min.
The invention provides a glass-ceramic system ceramic substrate material with adjustable shrinkage rate, which is prepared by the following steps ofThe raw materials of the controlled glass-ceramic system ceramic substrate material comprise: caO-B 2 O 3 -SiO 2 Is glass ceramics A, caO-B 2 O 3 -SiO 2 Is glass-ceramic B, caSiO 3 Base ceramic powder, solvent, dispersant, plasticizer and resin; the CaO-B is 2 O 3 -SiO 2 Is glass ceramics A, caO-B 2 O 3 -SiO 2 Glass ceramics B and CaSiO 3 The mass ratio of the base ceramic powder is (60-80): (10-30): (5-20); preparation of the CaO-B 2 O 3 -SiO 2 The microcrystalline glass A comprises the following raw materials: caCO (CaCO) 3 、H 3 BO 3 、SiO 2 MgO and La 2 O 3 The method comprises the steps of carrying out a first treatment on the surface of the Preparation of the CaO-B 2 O 3 -SiO 2 The microcrystalline glass B comprises the following raw materials: caCO (CaCO) 3 、H 3 BO 3 、SiO 2 And Al 2 O 3 . The invention uses CaO-B 2 O 3 -SiO 2 The microcrystalline glass is used as raw material, and CaSiO can be precipitated in the sintering process 3 Crystalline phase and CaB 2 O 4 The CBS microcrystalline glass with different components, different softening temperatures and different crystallization characteristics is adopted as a crystalline phase, so that the shrinkage behavior of the substrate in the sintering process can be regulated and controlled, and the sintering warping phenomenon of the substrate and LTCC series slurry can be improved; whereas CaO-B 2 O 3 -SiO 2 MgO and La in glass ceramics A 2 O 3 The composite use can play a role in synergism, promote crystallization in the sintering process, reduce the content of glass phase in a sintered system and effectively reduce dielectric loss; adopts CBS microcrystalline glass and CaSiO 3 The composite system can increase the flatness and matching property of the co-firing of the substrate material and the LTCC slurry through the skeleton effect of the ceramic in the matrix; at the same time CaSiO 3 Has relatively low dielectric constant, and is used for CaO-B 2 O 3 -SiO 2 CaSiO is added into the system microcrystalline glass 3 The dielectric constant of the substrate can be effectively regulated and controlled by the base ceramic powder. The results of the examples show that the X/Y shrinkage of the LTCC substrate material provided by the invention is controllable within 10-15%, the dielectric constant is 5.8-6.2 at 1MHz, and the dielectric loss is less than or equal to 3X 10 -3 。
Drawings
FIG. 1 shows CaO-B as provided by the invention 2 O 3 -SiO 2 Microcrystalline glass A-1 and CaO-B 2 O 3 -SiO 2 A DSC curve of microcrystalline glass A-2;
FIG. 2 shows CaO-B as the present invention 2 O 3 -SiO 2 Microcrystalline glass B-1 and CaO-B 2 O 3 -SiO 2 Is the DSC curve of the microcrystalline glass B-2.
Detailed Description
The invention provides a glass-ceramic system ceramic substrate material with adjustable shrinkage, which is prepared from the following raw materials: caO-B 2 O 3 -SiO 2 Is glass ceramics A, caO-B 2 O 3 -SiO 2 Is glass-ceramic B, caSiO 3 Base ceramic powder, solvent, dispersant, plasticizer and resin;
the CaO-B is 2 O 3 -SiO 2 Is glass ceramics A, caO-B 2 O 3 -SiO 2 Glass ceramics B and CaSiO 3 The mass ratio of the base ceramic powder is (60-80): (10-30): (5-20);
preparation of the CaO-B 2 O 3 -SiO 2 The microcrystalline glass A comprises the following raw materials: caCO (CaCO) 3 、H 3 BO 3 、SiO 2 MgO and La 2 O 3 ；
Preparation of the CaO-B 2 O 3 -SiO 2 The microcrystalline glass B comprises the following raw materials: caCO (CaCO) 3 、H 3 BO 3 、SiO 2 And Al 2 O 3 。
In the invention, the raw materials for preparing the glass-ceramic system ceramic substrate material with adjustable shrinkage rate comprise CaO-B 2 O 3 -SiO 2 Microcrystalline glass A is used for preparing the CaO-B 2 O 3 -SiO 2 The microcrystalline glass A comprises the following raw materials: caCO (CaCO) 3 、H 3 BO 3 、SiO 2 MgO and La 2 O 3 。
In the present invention, the CaCO 3 、H 3 BO 3 、SiO 2 MgO and La 2 O 3 The mass ratio of (2) is preferably (40-70): (15-30): (20-35): (0.5-2): (0.5 to 3), more preferably (45 to 65): (20-25): (25-30): (1-1.5): (1 to 2.5), more preferably (50 to 60): (20-25): (25-30): (1-1.5): (1.5-2). The invention is implemented by mixing CaO-B 2 O 3 -SiO 2 The usage amount of each raw material in the glass ceramic A is controlled within the above range, and CaSiO can be further promoted 3 The base ceramic powder is devitrified in the sintering process, so that the content of a glass phase in a system after sintering is reduced, and the dielectric loss is further reduced.
In the present invention, the CaCO 3 、H 3 BO 3 、SiO 2 MgO and La 2 O 3 Preferably analytically pure CaCO 3 、H 3 BO 3 、SiO 2 MgO and La 2 O 3 . The invention aims at CaCO 3 、H 3 BO 3 、SiO 2 MgO and La 2 O 3 The specific source of (c) is not particularly limited, and may be commercially available products known to those skilled in the art or may be self-prepared. According to the invention, the raw materials are controlled to be of an analytical grade, so that the influence of impurities on the microcrystalline glass can be reduced.
In the present invention, the CaO-B is 2 O 3 -SiO 2 The preparation method of the glass ceramics A preferably comprises the following steps:
1) CaCO is put into 3 、H 3 BO 3 、SiO 2 MgO and La 2 O 3 Mixing to obtain mixed powder;
2) Sequentially melting, water quenching, ball milling, sieving and drying the mixed powder obtained in the step 1) to obtain CaO-B 2 O 3 -SiO 2 Is microcrystalline glass A.
The invention preferably uses CaCO 3 、H 3 BO 3 、SiO 2 MgO and La 2 O 3 Mixing to obtain mixed powder. The manner of mixing is not particularly limited in the present invention,can mix the components uniformly.
After the mixed powder is obtained, the mixed powder is preferably subjected to melting, water quenching, ball milling, sieving and drying in sequence to obtain CaO-B 2 O 3 -SiO 2 Is microcrystalline glass A.
In the present invention, the melting temperature is preferably 1300 to 1500 ℃, more preferably 1350 to 1450 ℃, still more preferably 1400 ℃; the holding time for the melting is preferably 1.5 to 3 hours, more preferably 2 to 2.5 hours. The rate of temperature rise to the melting temperature is not particularly limited, and may be determined according to the technical knowledge of those skilled in the art. In the present invention, the melting is preferably performed in a platinum crucible. The invention can fully melt and mix the raw materials by controlling the melting parameters.
In the present invention, the water quenching is preferably performed in deionized water; the water quench is preferably pouring the molten product into deionized water. The rate at which the molten product is poured into deionized water is not particularly limited in the present invention, and may be determined according to the technical common knowledge of those skilled in the art. The invention can quickly quench the molten glass liquid to form a glass body by a water quenching mode.
In the present invention, the ball milling is preferably performed in a ball mill. The specific type of the ball mill is not particularly limited, and commercially available products known to those skilled in the art may be used.
In the present invention, the rotation speed of the ball mill is preferably 400 to 500rpm, more preferably 450rpm; the time of the ball milling is preferably 10 to 15 hours, more preferably 12 hours. According to the invention, through controlling the ball milling parameters, the glass body after water quenching can be broken into fine microcrystalline glass.
The invention is not particularly limited to the specific operation of sieving, and CaO-B can be obtained 2 O 3 -SiO 2 The granularity of the microcrystalline glass A meets the requirement. The invention can remove the microcrystalline glass with larger grain size by sieving, thereby ensuring that the grain size of the microcrystalline glass meets the requirement.
In the present invention, the temperature of the dryingPreferably 60 to 100 ℃, more preferably 70 to 90 ℃, and even more preferably 80 ℃. In the present invention, the drying is preferably performed in an oven. The specific type of the oven is not particularly limited, and commercially available products known to those skilled in the art may be used. The drying time is not particularly limited, and CaO-B can be used 2 O 3 -SiO 2 And drying the microcrystalline glass A.
In the invention, the raw materials for preparing the glass-ceramic system ceramic substrate material with adjustable shrinkage rate also comprise CaO-B 2 O 3 -SiO 2 Microcrystalline glass B is used for preparing the CaO-B 2 O 3 -SiO 2 The microcrystalline glass B comprises the following raw materials: caCO (CaCO) 3 、H 3 BO 3 、SiO 2 And Al 2 O 3 。
In the present invention, the CaCO 3 、H 3 BO 3 、SiO 2 And Al 2 O 3 The mass ratio of (2) is preferably (15-30): (15-30): (20-40): (5 to 20), more preferably (20 to 25): (20-25): (25-35): (10-15). The invention is implemented by mixing CaO-B 2 O 3 -SiO 2 The usage amount of each raw material in the microcrystalline glass B is controlled within the range, and the shrinkage behavior of the substrate in the sintering process can be further regulated, so that the sintering warping phenomenon of the substrate and LTCC series slurry co-sintering is improved.
In the present invention, the CaCO 3 、H 3 BO 3 、SiO 2 And Al 2 O 3 Preferably analytically pure CaCO 3 、H 3 BO 3 、SiO 2 And Al 2 O 3 . The invention aims at CaCO 3 、H 3 BO 3 、SiO 2 And Al 2 O 3 The specific source of (c) is not particularly limited, and may be commercially available products known to those skilled in the art or may be self-prepared. According to the invention, the raw materials are controlled to be of an analytical grade, so that the influence of impurities on the microcrystalline glass can be reduced.
In the present invention, the CaO-B is 2 O 3 -SiO 2 Preparation of glass ceramics BThe preparation method preferably comprises the following steps:
I. CaCO is put into 3 、H 3 BO 3 、SiO 2 And Al 2 O 3 Mixing to obtain mixed powder;
II. And (3) sequentially carrying out melting, water quenching, ball milling, sieving and drying on the mixed powder obtained in the step (I) to obtain CaO-B 2 O 3 -SiO 2 Is microcrystalline glass B.
The invention preferably uses CaCO 3 、H 3 BO 3 、SiO 2 And Al 2 O 3 Mixing to obtain mixed powder. The mixing mode is not particularly limited, and the components can be uniformly mixed.
After the mixed powder is obtained, the mixed powder is preferably subjected to melting, water quenching, ball milling, sieving and drying in sequence to obtain CaO-B 2 O 3 -SiO 2 Is microcrystalline glass B.
In the present invention, the melting temperature is preferably 1300 to 1500 ℃, more preferably 1350 to 1450 ℃, still more preferably 1400 ℃; the holding time for the melting is preferably 1.5 to 3 hours, more preferably 2 to 2.5 hours. The rate of temperature rise to the melting temperature is not particularly limited, and may be determined according to the technical knowledge of those skilled in the art. In the present invention, the melting is preferably performed in a platinum crucible. The invention can fully melt and mix the raw materials by controlling the melting parameters.
In the present invention, the water quenching is preferably performed in deionized water; the water quench is preferably pouring the molten product into deionized water. The rate at which the molten product is poured into deionized water is not particularly limited in the present invention, and may be determined according to the technical common knowledge of those skilled in the art. The invention can quickly quench the molten glass liquid to form a glass body by a water quenching mode.
In the present invention, the ball milling is preferably performed in a ball mill. The specific type of the ball mill is not particularly limited, and commercially available products known to those skilled in the art may be used.
In the present invention, the rotation speed of the ball mill is preferably 400 to 500rpm, more preferably 450rpm; the time of the ball milling is preferably 10 to 15 hours, more preferably 12 hours. According to the invention, through controlling the ball milling parameters, the glass body after water quenching can be broken into fine microcrystalline glass.
The invention is not particularly limited to the specific operation of sieving, and CaO-B can be obtained 2 O 3 -SiO 2 The granularity of the microcrystalline glass B meets the requirement. The invention can remove the microcrystalline glass with larger grain size by sieving, thereby ensuring that the grain size of the microcrystalline glass meets the requirement.
In the present invention, the temperature of the drying is preferably 60 to 100 ℃, more preferably 70 to 90 ℃, and even more preferably 80 ℃. In the present invention, the drying is preferably performed in an oven. The specific type of the oven is not particularly limited, and commercially available products known to those skilled in the art may be used. The drying time is not particularly limited, and CaO-B can be used 2 O 3 -SiO 2 And drying the microcrystalline glass B.
In the invention, the raw materials for preparing the glass-ceramic system ceramic substrate material with adjustable shrinkage rate also comprise CaSiO 3 And (3) base ceramic powder. The invention is implemented by the method of CaO-B 2 O 3 -SiO 2 CaSiO is added into the glass ceramics 3 The dielectric constant of the substrate can be effectively regulated and controlled by the base ceramic powder.
In the present invention, the CaSiO 3 The base ceramic powder is preferably Ca 1-x Cu x SiO 3 The ceramic powder, wherein x is more than or equal to 0 and less than or equal to 0.025, preferably is more than or equal to 0.005 and less than or equal to 0.02, and more preferably is more than or equal to 0.01 and less than or equal to 0.015. The invention is realized by the method that the catalyst is prepared by the method of preparing the catalyst in CaSiO 3 The sintering temperature can be reduced from 1200 ℃ to 1125 ℃ by introducing Cu doping into the base ceramic powder, and the doped CaSiO 3 The base ceramic powder is single-phase beta-CaSiO after sintering 3 The ceramic can effectively adjust the dielectric property of a glass-ceramic system; by reacting CaSiO with 3 Cu doping amount and Cu doping CaSiO in base ceramic powder 3 The CaO-B can be effectively regulated by regulating the compounding amount with the microcrystalline glass 2 O 3 -SiO 2 Glass ceramics and CaSiO 3 Sintering property and dielectric property of LTCC substrate material prepared by the base ceramic powder.
In the present invention, the CaSiO is prepared 3 The raw materials of the base ceramic powder preferably comprise CaCO 3 、SiO 2 And CuO. In the present invention, the CaCO 3 、SiO 2 And CuO are preferably analytically pure CaCO 3 、SiO 2 And CuO. The invention aims at CaCO 3 、SiO 2 And CuO, are not particularly limited, and may be prepared by using commercially available products known to those skilled in the art or by themselves. The invention can reduce the influence caused by impurities by controlling the raw materials to be of an analytical grade.
In the present invention, the CaSiO 3 The preparation method of the base ceramic powder preferably comprises the following steps:
(1) CaCO is put into 3 、SiO 2 Mixing with CuO to obtain first mixed powder;
(2) sequentially performing first ball milling, first drying and grinding treatment on the first mixed powder obtained in the step (1) to obtain second mixed powder;
(3) calcining, ball milling, sieving and drying the second mixed powder obtained in the step (2) for the second time in sequence to obtain CaSiO 3 And (3) base ceramic powder.
The invention preferably uses CaCO 3 、SiO 2 And CuO to obtain a first mixed powder. In the present invention, the mixing is preferably performed in a three-dimensional mixer, and the specific model of the three-dimensional mixer is not particularly limited, and commercially available products known to those skilled in the art may be used. In the present invention, the mixing time is preferably 30 to 60 minutes, more preferably 40 to 50 minutes. According to the invention, through the mixing, the raw materials can be primarily and uniformly mixed.
After the first mixed powder is obtained, the first mixed powder is preferably subjected to ball milling, drying and grinding for the first time in sequence to obtain the second mixed powder.
In the present invention, the dispersant for the first ball milling is preferably deionized water; the ball milling medium for the first ball milling is preferably zirconia balls; the mass ratio of the ball milling medium, the first mixed powder and the dispersing agent is preferably 3:1:1, a step of; the rotating speed of the first ball milling is preferably 200-400 r/min, more preferably 300r/min; the ball milling time of the first ball milling is preferably 3 to 6 hours, more preferably 4 to 5 hours. According to the invention, through the first ball milling, the particle size of the raw materials can be reduced, and the raw materials are fully mixed, so that ceramic powder with uniform and excellent performance can be conveniently obtained in the subsequent calcination.
In the present invention, the temperature of the first drying is preferably 60 to 100 ℃, more preferably 70 to 90 ℃, still more preferably 80 ℃; the time for the first drying is preferably 10 to 20 hours, more preferably 12 to 18 hours, and still more preferably 15 to 16 hours. In the present invention, the first drying is preferably performed in an oven. The specific type of the oven is not particularly limited, and commercially available products known to those skilled in the art may be used. The invention can remove the dispersing agent in the mixed powder by drying.
The specific mode of the grinding treatment is not particularly limited in the present invention, and the mixed powder may be uniformly dispersed.
After the second mixed powder is obtained, the invention preferably carries out calcination, second ball milling, sieving and second drying on the second mixed powder in sequence to obtain CaSiO 3 And (3) base ceramic powder.
In the present invention, the temperature of the calcination is preferably 1100 to 1400 ℃, more preferably 1200 to 1300 ℃; the heat preservation time of the calcination is preferably 1.5-3 h, more preferably 2-2.5 h; the rate of temperature rise to the calcination temperature is preferably 5 ℃/min. In the present invention, the calcination is preferably performed in a box furnace. The specific model of the box-type furnace is not particularly limited, and commercially available products known to those skilled in the art can be used. According to the invention, by controlling the calcination parameters, the calcined ceramic has better compactness.
In the present invention, the manner of the second ball milling is preferably the same as that of the first ball milling, and will not be described herein.
In the present invention, the sieving is preferably a 500 mesh sieve. The invention can remove the ceramic powder with larger particle size by sieving treatment, thereby ensuring that the particle size of the ceramic powder meets the requirement.
In the present invention, the manner of the second drying is preferably the same as that of the first drying, and will not be described herein.
In the present invention, the CaO-B is 2 O 3 -SiO 2 Is glass ceramics A, caO-B 2 O 3 -SiO 2 Glass ceramics B and CaSiO 3 The base ceramic powders preferably all need to be sieved by a 500-mesh sieve. The invention is implemented by mixing CaO-B 2 O 3 -SiO 2 Is glass ceramics A, caO-B 2 O 3 -SiO 2 Glass ceramics B and CaSiO 3 The base ceramic powder is screened by a 500-mesh screen, so that the granularity of microcrystalline glass and ceramic powder can be controlled, the compactness of the ceramic substrate material can be further improved in the sintering process, and the dielectric property of the ceramic substrate material can be improved.
In the present invention, the CaO-B is 2 O 3 -SiO 2 Is glass ceramics A, caO-B 2 O 3 -SiO 2 Glass ceramics B and CaSiO 3 The mass ratio of the base ceramic powder is (60-80): (10-30): (5 to 20), preferably (65 to 75): (15-25): (10 to 15), more preferably (70 to 75): (20-25): (10-15). The invention can effectively regulate CaO-B by controlling the dosage relation of microcrystalline glass and ceramic powder 2 O 3 -SiO 2 Glass ceramics and CaSiO 3 Sintering property and dielectric property of LTCC substrate material prepared by the base ceramic powder.
In the invention, the raw materials for preparing the glass-ceramic system ceramic substrate material with the adjustable shrinkage rate also comprise a solvent, a dispersing agent, a plasticizer and a resin. In the present invention, the solvent preferably includes two or three of ethanol, acetone, and xylene; the dispersing agent is preferably one or two of castor oil and oleic acid; the plasticizer is preferably dibutyl phthalate; the resin is preferably polyvinyl butyral. The specific sources of the solvent, dispersant, plasticizer and resin are not particularly limited in the present invention, and commercially available products known to those skilled in the art may be used.
In the present invention, the mass ratio of the solvent, the dispersant, the plasticizer and the resin is preferably (80 to 120): 1: (4-8): (10 to 20), more preferably (90 to 110): 1: (5-7): (12 to 18), more preferably (90 to 100): 1: (5-6): (14-15); the total mass of the solvent, the dispersing agent, the plasticizer and the resin is equal to CaO-B 2 O 3 -SiO 2 Is glass ceramics A, caO-B 2 O 3 -SiO 2 Glass ceramics B and CaSiO 3 The ratio of the total mass of the base ceramic powder is preferably (40-60): (60 to 40), more preferably (45 to 55): (55 to 45), more preferably 50:50. the invention can further improve the dielectric property of the ceramic substrate material by controlling the dosage of each component in the range.
In the invention, the prepared glass-ceramic system ceramic substrate material with adjustable shrinkage rate has good cofiring matching performance with LTCC slurry. Printing LTCC slurry on a raw ceramic film, co-firing, and flattening the substrate after co-firing. The specific components and sources of the LTCC slurry are not particularly limited, and the LTCC slurry is selected according to production requirements, such as gold slurry or silver slurry. The specific operation of the printing LTCC slurry is not particularly limited in the present invention, and may be determined according to the technical common knowledge of those skilled in the art.
The invention uses CaO-B 2 O 3 -SiO 2 The microcrystalline glass is used as raw material, and CaSiO can be precipitated in the sintering process 3 Crystalline phase and CaB 2 O 4 The CBS microcrystalline glass with different components, different softening temperatures and different crystallization characteristics is adopted as a crystalline phase, so that the shrinkage behavior of the substrate in the sintering process can be regulated and controlled, and the sintering warping phenomenon of the substrate and LTCC series slurry can be improved; whereas CaO-B 2 O 3 -SiO 2 MgO and La in glass ceramics A 2 O 3 The composite use can play a role in synergism, promote crystallization in the sintering process, reduce the content of glass phase in a sintered system and effectively reduce dielectric loss; adopts CBS microcrystalline glass and CaSiO 3 Composite systems, by the "skeleton" effect of ceramics in the matrixThe flatness and the matching performance of the co-firing of the substrate material and the LTCC slurry can be improved; at the same time CaSiO 3 Has relatively low dielectric constant, and is used for CaO-B 2 O 3 -SiO 2 CaSiO is added into the system microcrystalline glass 3 The dielectric constant of the substrate can be effectively regulated and controlled by the base ceramic powder.
The invention provides a preparation method of a glass-ceramic system ceramic substrate material with adjustable shrinkage, which comprises the following steps:
(1) CaO-B 2 O 3 -SiO 2 Is glass ceramics A, caO-B 2 O 3 -SiO 2 Is glass-ceramic B, caSiO 3 Mixing the base ceramic powder, a solvent, a dispersing agent, a plasticizer and resin to obtain ceramic slurry;
(2) Casting the ceramic slurry obtained in the step (1) into a green ceramic tape, and then sequentially cutting, laminating and carrying out temperature isostatic pressing to obtain a green body of the glass-ceramic system ceramic substrate;
(3) And (3) sequentially discharging glue and sintering the green body of the glass-ceramic system ceramic substrate obtained in the step (2) to obtain the glass-ceramic system ceramic substrate material with adjustable shrinkage rate.
The invention uses CaO-B 2 O 3 -SiO 2 Is glass ceramics A, caO-B 2 O 3 -SiO 2 Is glass-ceramic B, caSiO 3 Mixing the base ceramic powder, the solvent, the dispersing agent, the plasticizer and the resin to obtain ceramic slurry.
In the present invention, the mixing means is preferably ball milling; the rotation speed of the ball mill is preferably 100-200 rpm, more preferably 150rpm; the ball milling time is preferably 70 to 75 hours, more preferably 72 hours. The invention can mix the components more uniformly by ball milling and mixing, and can adjust the viscosity of the ceramic slurry.
After ball milling is completed, the ball-milled product is preferably subjected to filtration and deaeration in sequence. The specific operations of the filtration and deaeration treatment are not particularly limited, and may be determined according to the technical common knowledge of a person skilled in the art. The invention can remove ball milling medium and bubbles in the ceramic slurry through filtration and defoaming treatment, thereby avoiding the influence of the bubbles on the quality of the green ceramic film.
In the present invention, the viscosity of the ceramic slurry is preferably 2 to 3pa·s. The invention controls the viscosity of the ceramic slurry in the above range, so that the ceramic slurry has better viscosity and fluidity, thereby facilitating the subsequent casting.
After ceramic slurry is obtained, the ceramic slurry is cast into a green ceramic tape, and then cutting, lamination and temperature isostatic pressing are sequentially carried out, so that a green body of the glass-ceramic system ceramic substrate is obtained.
In the present invention, the casting is preferably performed on a casting machine. The type of the casting machine is not particularly limited, and commercially available products known to those skilled in the art may be used. The specific operation of the casting is not particularly limited in the present invention, and may be determined according to the technical common knowledge of a person skilled in the art.
The specific operation of the cutting is not particularly limited in the present invention, and the cutting may be performed in a manner well known to those skilled in the art according to the size of the desired green glass-ceramic substrate.
In the invention, when the glass-ceramic system ceramic substrate material with adjustable shrinkage rate and the LTCC slurry are required to be co-fired, the step of printing the LTCC slurry is preferably performed after cutting is finished, namely, the ceramic slurry is cast into a green ceramic tape, and then cutting, printing the LTCC slurry, laminating and temperature isostatic pressing are sequentially performed to obtain the glass-ceramic system ceramic substrate green body with the LTCC slurry printed. The invention can verify the cofiring matching property of the ceramic substrate material and the LTCC slurry by cofiring the ceramic substrate material and the LTCC slurry.
The specific operation of the laminate is not particularly limited, and may be determined according to the technical knowledge of those skilled in the art.
In the present invention, the temperature of the warm isostatic pressing is preferably 60 to 80 ℃, more preferably 60 to 75 ℃, further preferably 70 ℃; the pressure of the warm isostatic pressing is preferably 15 to 25MPa, more preferably 18 to 23MPa, and even more preferably 20MPa; the time for the warm isostatic pressing is preferably 30 to 60 minutes, more preferably 40 to 50 minutes. The invention can further improve the compactness of the low-temperature co-fired ceramic substrate material of the glass-ceramic system through temperature isostatic pressing.
After the glass-ceramic system ceramic substrate green compact is obtained, the glass-ceramic system ceramic substrate green compact is sequentially subjected to glue discharging and sintering, and the glass-ceramic system ceramic substrate material with adjustable shrinkage rate is obtained.
In the invention, the temperature of the adhesive discharge is preferably 450-600 ℃, more preferably 500-550 ℃; the time for discharging the adhesive is preferably 1 to 3 hours, more preferably 2 hours. According to the invention, through the glue discharging treatment, organic substances such as adhesive and the like in the green body of the ceramic substrate of the glass-ceramic system can be burned out in advance, so that the subsequent sintering of the ceramic is facilitated.
In the present invention, the sintering temperature is preferably 800 to 950 ℃, more preferably 850 to 900 ℃; the sintering heat preservation time is preferably 10-30 min, more preferably 15-25 min, and even more preferably 20min; the cooling mode of sintering is preferably furnace-following cooling. The invention can ensure that the ceramic substrate material has good compactness through low-temperature short-time sintering.
The preparation method is simple, the used equipment is conventional equipment for preparing the ceramic substrate material, new equipment is not needed, and the production cost is reduced; meanwhile, the sintering temperature in the preparation process is low, the sintering time is short, the loss of equipment is reduced, and the method is favorable for large-scale popularization of industry.
The technical solutions of the present invention will be clearly and completely described in the following in connection with the embodiments of the present invention. It will be apparent that the described embodiments are only some, but not all, embodiments of the invention. All other embodiments, which can be made by those skilled in the art based on the embodiments of the invention without making any inventive effort, are intended to be within the scope of the invention.
In the examples of the present invention, caO-B 2 O 3 -SiO 2 The preparation of the glass ceramics A comprises the following steps:
1) Analytically pure CaCO 3 、H 3 BO 3 、SiO 2 MgO and La 2 O 3 Mixing to obtain mixed powder;
2) Putting the mixed powder obtained in the step 1) into a platinum crucible for melting, pouring the melted product into deionized water for water quenching, putting into a ball mill for ball milling, sieving with a 500-mesh sieve, and finally drying in an oven to obtain CaO-B 2 O 3 -SiO 2 Is microcrystalline glass A; the melting temperature is 1400 ℃, and the melting heat preservation time is 2 hours; the rotation speed of the ball milling is 450rpm, and the ball milling time is 12 hours; the temperature of the drying is 80 ℃.
When CaCO 3 、H 3 BO 3 、SiO 2 MgO and La 2 O 3 The mass ratio of (2) is 50:25:23:1:1 to obtain CaO-B 2 O 3 -SiO 2 Microcrystalline glass A-1;
when CaCO 3 、H 3 BO 3 、SiO 2 MgO and La 2 O 3 The mass ratio of (2) is 50:23:22:2:3, caO-B is obtained 2 O 3 -SiO 2 Microcrystalline glass A-2;
for CaO-B respectively 2 O 3 -SiO 2 Microcrystalline glass A-1 and CaO-B 2 O 3 -SiO 2 DSC test is carried out on the glass ceramics A-2 to obtain the softening point and crystallization peak temperature of the glass, wherein CaO-B 2 O 3 -SiO 2 Microcrystalline glass A-1 and CaO-B 2 O 3 -SiO 2 The composition ratios and softening points of the microcrystalline glass A-2 are shown in Table 1:
TABLE 1 CaO-B 2 O 3 -SiO 2 Microcrystalline glass A-1 and CaO-B 2 O 3 -SiO 2 Component proportion and softening point of glass ceramics A-2
| Microcrystalline glass | CaCO 3 | H 3 BO 3 | SiO 2 | MgO | La 2 O 3 | T g (℃) |
| CaO-B 2 O 3 -SiO 2 Glass ceramics A-1 | 50 | 25 | 23 | 1 | 1 | 745 |
| CaO-B 2 O 3 -SiO 2 Glass ceramics A-2 | 50 | 23 | 22 | 2 | 3 | 750 |
CaO-B 2 O 3 -SiO 2 Microcrystalline glass A-1 and CaO-B 2 O 3 -SiO 2 The DSC curve of the glass-ceramic A-2 is shown in FIG. 1. As can be seen from FIG. 1, with CaO-B 2 O 3 -SiO 2 CaCO in glass ceramics A 3 、H 3 BO 3 、SiO 2 MgO and La 2 O 3 Change of mass ratio, caO-B 2 O 3 -SiO 2 The crystallization peak temperature of the glass ceramic A also changes, but the change amplitude is smaller.
In the examples of the present invention, caO-B 2 O 3 -SiO 2 The preparation of the glass ceramics B comprises the following steps:
1) Will analyze pure CaCO 3 、H 3 BO 3 、SiO 2 And Al 2 O 3 Mixing to obtain mixed powder;
2) Putting the mixed powder obtained in the step 1) into a platinum crucible for melting, pouring the melted product into deionized water for water quenching, putting into a ball mill for ball milling, sieving with a 500-mesh sieve, and finally drying in an oven to obtain CaO-B 2 O 3 -SiO 2 Glass ceramics B; the melting temperature is 1400 ℃, and the melting heat preservation time is 2 hours; the rotation speed of the ball milling is 450rpm, and the ball milling time is 12 hours; the temperature of the drying is 80 ℃.
When CaCO 3 、H 3 BO 3 、SiO 2 And Al 2 O 3 The mass ratio of (2) is 30:25:35:10 to obtain CaO-B 2 O 3 -SiO 2 Microcrystalline glass B-1;
when CaCO 3 、H 3 BO 3 、SiO 2 And Al 2 O 3 The mass ratio of (2) is 30:23:30:15, caO-B is obtained 2 O 3 -SiO 2 Microcrystalline glass B-2;
for CaO-B respectively 2 O 3 -SiO 2 Microcrystalline glass B-1 and CaO-B 2 O 3 -SiO 2 DSC test is carried out on the glass B-2, thus obtaining the softening point and crystallization peak temperature of the glass, wherein CaO-B 2 O 3 -SiO 2 Microcrystalline glass B-1 and CaO-B 2 O 3 -SiO 2 The composition ratios and softening points of the glass ceramics B-2 are shown in Table 2:
TABLE 2 CaO-B 2 O 3 -SiO 2 Microcrystalline glass B-1 and CaO-B 2 O 3 -SiO 2 Component proportion and softening point of glass ceramics B-2
| Microcrystalline glass | CaCO 3 | H 3 BO 3 | SiO 2 | Al 2 O 3 | T g (℃) |
| CaO-B 2 O 3 -SiO 2 Glass ceramics B-1 | 30 | 25 | 35 | 10 | 786 |
| CaO-B 2 O 3 -SiO 2 Glass ceramics B-2 | 32 | 23 | 30 | 15 | 782 |
CaO-B 2 O 3 -SiO 2 Microcrystalline glass B-1 and CaO-B 2 O 3 -SiO 2 The DSC curve of the glass-ceramic B-2 is shown in FIG. 2. As can be seen from FIG. 2, following CaO-B 2 O 3 -SiO 2 CaCO in glass ceramics B 3 、H 3 BO 3 、SiO 2 And Al 2 O 3 Change of mass ratio, caO-B 2 O 3 -SiO 2 No obvious crystallization peak exists in the microcrystalline glass B.
In an embodiment of the invention, the CaSiO 3 The base ceramic powder is Ca 1-x Cu x SiO 3 Ceramic powder, the Ca 1- x Cu x SiO 3 The preparation of the ceramic powder comprises the following steps:
(1) CaCO is put into 3 、SiO 2 Mixing with CuO in a three-dimensional mixer for 40min to obtain first mixed powder;
(2) sequentially performing first ball milling, first drying and grinding treatment on the first mixed powder obtained in the step (1) to obtain second mixed powder; the dispersing agent for the first ball milling is deionized water; the ball milling medium for the first ball milling is zirconia balls; the mass ratio of the ball milling medium to the first mixed powder to the dispersing agent is 3:1:1, a step of; the rotating speed of the first ball milling is 300r/min, and the ball milling time of the first ball milling is 4h; the primary drying is carried out in an oven, the temperature of the primary drying is 80 ℃, and the time of the primary drying is 15 hours;
(3) calcining the second mixed powder obtained in the step (2), ball milling for the second time, sieving with a 500-mesh sieve and drying for the second time in sequence to obtain CaSiO 3 A base ceramic powder; the calcination is carried out in a box-type furnace, and the temperature of the calcination is 1300 ℃; the heat preservation time of calcination is 2h; the heating rate for heating to the calcination temperature is 5 ℃/min; the rotating speed of the second ball milling is 300r/min, and the ball milling time of the second ball milling is 4h; the second drying is carried out in an oven, the temperature of the second drying is 80 ℃, and the time of the second drying is 15 hours.
When Ca is 1-x Cu x SiO 3 When x in the ceramic powder is 0, 0.005, 0.01, 0.015, 0.02 and 0.025 respectively, the prepared CaSiO 3 The base ceramic powders were C-1, C-2, C-3, C-4, C-5 and C-6, respectively, as shown in Table 3:
TABLE 3 CaSiO 3 Base ceramic powder
| CaSiO 3 Base ceramic powder | Ceramic component |
| C-1 | CaSiO 3 |
| C-2 | Ca 0.095 Cu 0.005 SiO 3 |
| C-3 | Ca 0.09 Cu 0.01 SiO 3 |
| C-4 | Ca 0.085 Cu 0.015 SiO 3 |
| C-5 | Ca 0.08 Cu 0.02 SiO 3 |
| C-6 | Ca 0.075 Cu 0.025 SiO 3 |
Example 1
The raw materials for preparing the glass-ceramic system ceramic substrate material with adjustable shrinkage rate are as follows: caO-B 2 O 3 -SiO 2 Microcrystalline glass A-1, caO-B 2 O 3 -SiO 2 Microcrystalline glass B-1, caSiO 3 Base ceramic powder C-1, a solvent, a dispersing agent, a plasticizer and a resin;
the CaO-B is 2 O 3 -SiO 2 Microcrystalline glass A-1, caO-B 2 O 3 -SiO 2 Microcrystalline glass B-1 and CaSiO 3 The mass ratio of the base ceramic powder C-1 is 65:25:10;
the solvent is ethanol and acetone, and the volume ratio of the ethanol to the acetone is 1:1, a step of; the dispersing agent is castor oil; the plasticizer is dibutyl phthalate; the resin is polyvinyl butyral; the mass ratio of the solvent to the dispersant to the plasticizer to the resin is 100:1:6:15; the total mass of the solvent, the dispersing agent, the plasticizer and the resin is equal to CaO-B 2 O 3 -SiO 2 Microcrystalline glass A-1, caO-B 2 O 3 -SiO 2 Microcrystalline glass B-1 and CaSiO 3 The ratio of the total mass of the base ceramic powder C-1 is 50:50;
the preparation method of the glass-ceramic system ceramic substrate material with adjustable shrinkage rate comprises the following steps:
(1) CaO-B 2 O 3 -SiO 2 Microcrystalline glass A-1, caO-B 2 O 3 -SiO 2 Microcrystalline glass B-1, caSiO 3 Mixing the base ceramic powder C-1, a solvent, a dispersing agent, a plasticizer and resin, and then sequentially carrying out filtration and defoaming treatment to obtain ceramic slurry; the mixing mode is ball milling, the rotation speed of the ball milling is 150rpm, and the ball milling time is 72 hours; the viscosity of the ceramic slurry is 2-3 Pa.S;
(2) Casting the ceramic slurry obtained in the step (1) into a green ceramic tape in a casting machine, and then sequentially cutting, laminating and carrying out temperature isostatic pressing to obtain a green body of the glass-ceramic system ceramic substrate; the temperature of the temperature isostatic pressing is 70 ℃, the pressure of the temperature isostatic pressing is 20MPa, and the time of the temperature isostatic pressing is 40min; the size of the green body of the glass-ceramic system ceramic substrate is 10 multiplied by 10cm;
(3) Sequentially discharging glue and sintering the green body of the glass-ceramic system ceramic substrate obtained in the step (2) to obtain a glass-ceramic system ceramic substrate material with adjustable shrinkage rate; the temperature of the glue discharging is 500 ℃, and the time of the glue discharging is 2 hours; the sintering temperature is 850 ℃, the sintering heat preservation time is 15min, and the cooling mode of sintering is furnace cooling.
Example 2
The raw materials for preparing the glass-ceramic system ceramic substrate material with adjustable shrinkage rate are as follows: caO-B 2 O 3 -SiO 2 Microcrystalline glass A-2, caO-B 2 O 3 -SiO 2 Microcrystalline glass B-1, caSiO 3 Base ceramic powder C-2, solvent, dispersant, plasticizer and resin;
other conditions were the same as in example 1.
Example 3
The raw materials for preparing the glass-ceramic system ceramic substrate material with adjustable shrinkage rate are as follows: caO-B 2 O 3 -SiO 2 Microcrystalline glass A-1, caO-B 2 O 3 -SiO 2 Microcrystalline glass B-2, caSiO 3 Base ceramic powder C-3, solvent, dispersant, plasticizer and resin;
other conditions were the same as in example 1.
Example 4
The raw materials for preparing the glass-ceramic system ceramic substrate material with adjustable shrinkage rate are as follows: caO-B 2 O 3 -SiO 2 Microcrystalline glass A-2, caO-B 2 O 3 -SiO 2 Microcrystalline glass B-2, caSiO 3 Base ceramic powder C-4, a solvent, a dispersing agent, a plasticizer and a resin;
the CaO-B is 2 O 3 -SiO 2 Microcrystalline glass A-2, caO-B 2 O 3 -SiO 2 Microcrystalline glass B-2 and CaSiO 3 The mass ratio of the base ceramic powder C-4 is 62:23:15;
other conditions were the same as in example 1.
The shrinkage of the glass-ceramic system ceramic substrate materials with adjustable shrinkage and the dielectric properties at 1MHz prepared in examples 1 to 4 were tested, and the results are shown in Table 4:
TABLE 4 shrinkage and dielectric Properties of the glass-ceramic System ceramic substrate materials with controlled shrinkage prepared in examples 1 to 4
| Examples | X/Y shrinkage (%) | Dielectric constant | Dielectric loss (. Times.10) -3 ) |
| Example 1 | 12.51 | 6.16 | 1.57 |
| Example 2 | 11.40 | 5.99 | 1.75 |
| Example 3 | 11.01 | 5.97 | 0.89 |
| Example 4 | 10.90 | 5.91 | 2.80 |
As can be seen from Table 4, the glass-ceramic system low-temperature cofired ceramic substrate material prepared by the invention can be prepared by adjusting and controlling CaO-B 2 O 3 -SiO 2 Is glass ceramics A, caO-B 2 O 3 -SiO 2 Glass ceramics B and CaSiO 3 The shrinkage rate of the base ceramic powder is regulated and controlled by the component proportion and the mass ratio of the base ceramic powder, and meanwhile, the prepared glass-ceramic system low-temperature co-fired ceramic substrate material has good dielectric property.
Example 5
The raw materials for preparing the glass-ceramic system ceramic substrate material with adjustable shrinkage rate are as follows: caO-B 2 O 3 -SiO 2 Microcrystalline glass A-1, caO-B 2 O 3 -SiO 2 Microcrystalline glass B-1, caSiO 3 Base ceramic powder C-1, a solvent, a dispersing agent, a plasticizer and a resin;
the CaO-B is 2 O 3 -SiO 2 Microcrystalline glass A-1, caO-B 2 O 3 -SiO 2 Microcrystalline glass B-1 and CaSiO 3 The mass ratio of the base ceramic powder C-1 is 65:25:10;
the solvent is ethanol and acetone, and the volume ratio of the ethanol to the acetone is 1:1, a step of; the dispersing agent is castor oil; the plasticizer is dibutyl phthalate; the resin is polyvinyl butyral; the mass ratio of the solvent to the dispersant to the plasticizer to the resin is 100:1:6:15; the total mass of the solvent, the dispersing agent, the plasticizer and the resin is equal to CaO-B 2 O 3 -SiO 2 Microcrystalline glass A-1, caO-B 2 O 3 -SiO 2 Microcrystalline glass B-1 and CaSiO 3 The ratio of the total mass of the base ceramic powder C-1 is 50:50;
the method for co-firing the glass-ceramic system ceramic substrate material with adjustable shrinkage and the LTCC slurry comprises the following steps:
(1) CaO-B 2 O 3 -SiO 2 Microcrystalline glass A-1, caO-B 2 O 3 -SiO 2 Microcrystalline glass B-1, caSiO 3 Mixing the base ceramic powder C-1, a solvent, a dispersing agent, a plasticizer and resin, and then sequentially carrying out filtration and defoaming treatment to obtain ceramic slurry; the mixing mode is ball milling, the rotation speed of the ball milling is 150rpm, and the ball milling time is 72 hours; the viscosity of the ceramic slurry is 2-3 Pa.S;
(2) Casting the ceramic slurry obtained in the step (1) into a green ceramic tape in a casting machine, and then sequentially cutting, printing LTCC slurry, laminating and carrying out temperature isostatic pressing to obtain a green body of the glass-ceramic system ceramic substrate; the LTCC slurry is gold slurry; the temperature of the temperature isostatic pressing is 70 ℃, the pressure of the temperature isostatic pressing is 20MPa, and the time of the temperature isostatic pressing is 40min; the size of the green body of the glass-ceramic system ceramic substrate is 10 multiplied by 10cm;
(3) Sequentially discharging glue and sintering the green body of the glass-ceramic system ceramic substrate obtained in the step (2) to obtain a glass-ceramic system ceramic substrate material with adjustable shrinkage rate; the temperature of the glue discharging is 500 ℃, and the time of the glue discharging is 2 hours; the sintering temperature is 850 ℃, the sintering heat preservation time is 15min, and the cooling mode of sintering is furnace cooling.
The foregoing is merely a preferred embodiment of the present invention and it should be noted that modifications and adaptations to those skilled in the art may be made without departing from the principles of the present invention, which are intended to be comprehended within the scope of the present invention.
Claims (8)
1. The raw materials for preparing the glass-ceramic system ceramic substrate material with adjustable shrinkage rate comprise the following components: caO-B 2 O 3 -SiO 2 Is glass ceramics A, caO-B 2 O 3 -SiO 2 Is glass-ceramic B, caSiO 3 Base ceramic powder, solvent, dispersant, plasticizer and resin;
the CaO-B is 2 O 3 -SiO 2 Glass ceramicsA, caO-B glass 2 O 3 -SiO 2 Glass ceramics B and CaSiO 3 The mass ratio of the base ceramic powder is (60-80): (10-30): (5-20);
preparation of the CaO-B 2 O 3 -SiO 2 The microcrystalline glass A comprises the following raw materials: caCO (CaCO) 3 、H 3 BO 3 、SiO 2 MgO and La 2 O 3 The method comprises the steps of carrying out a first treatment on the surface of the Preparation of the CaO-B 2 O 3 -SiO 2 CaCO in the raw material of glass ceramics A 3 、H 3 BO 3 、SiO 2 MgO and La 2 O 3 The mass ratio of (40-70): (15-30): (20-35): (0.5-2): (0.5-3);
preparation of the CaO-B 2 O 3 -SiO 2 The microcrystalline glass B comprises the following raw materials: caCO (CaCO) 3 、H 3 BO 3 、SiO 2 And Al 2 O 3 The method comprises the steps of carrying out a first treatment on the surface of the Preparation of the CaO-B 2 O 3 -SiO 2 CaCO in the material of glass ceramics B 3 、H 3 BO 3 、SiO 2 And Al 2 O 3 The mass ratio of (15-30): (15-30): (20-40): (5-20).
2. The shrinkage-controllable glass-ceramic system ceramic substrate material of claim 1, wherein the CaSiO 3 The base ceramic powder is Ca 1-x Cu x SiO 3 And the x is more than or equal to 0 and less than or equal to 0.025.
3. The shrinkage-controllable glass-ceramic system ceramic substrate material according to claim 1 or 2, wherein the CaSiO is prepared 3 The raw materials of the base ceramic powder comprise CaCO 3 、SiO 2 And CuO.
4. The shrinkage-controllable glass-ceramic system ceramic substrate material according to claim 1, wherein the CaO-B 2 O 3 -SiO 2 Is glass ceramics A, caO-B 2 O 3 -SiO 2 Glass ceramics B and CaSiO 3 The base ceramic powder is sieved by a 500-mesh sieve.
5. The shrinkage-controllable glass-ceramic system ceramic substrate material of claim 1, wherein the solvent comprises two or three of ethanol, acetone, and xylene; the dispersing agent is one or two of castor oil and oleic acid; the plasticizer is dibutyl phthalate; the resin is polyvinyl butyral.
6. The method for preparing the glass-ceramic system ceramic substrate material with adjustable shrinkage rate according to any one of claims 1 to 5, comprising the following steps:
(1) CaO-B 2 O 3 -SiO 2 Is glass ceramics A, caO-B 2 O 3 -SiO 2 Is glass-ceramic B, caSiO 3 Mixing the base ceramic powder, a solvent, a dispersing agent, a plasticizer and resin to obtain ceramic slurry;
(2) Casting the ceramic slurry obtained in the step (1) into a green ceramic tape, and then sequentially cutting, laminating and carrying out temperature isostatic pressing to obtain a green body of the glass-ceramic system ceramic substrate;
(3) And (3) sequentially discharging glue and sintering the green body of the glass-ceramic system ceramic substrate obtained in the step (2) to obtain the glass-ceramic system ceramic substrate material with adjustable shrinkage rate.
7. The method according to claim 6, wherein the temperature of the adhesive discharge in the step (3) is 450 to 600 ℃.
8. The method according to claim 6, wherein the sintering temperature in the step (3) is 800-950 ℃ and the sintering heat-preserving time is 10-30 min.
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Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109467415A (en) * | 2018-11-26 | 2019-03-15 | 中国电子科技集团公司第十三研究所 | The preparation method of low-temperature co-burning ceramic material composite substrate |
| EP4049981A1 (en) * | 2021-02-24 | 2022-08-31 | Ivoclar Vivadent AG | Glass ceramic with quartz mixed crystal phase |
Family Cites Families (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6844278B2 (en) * | 2001-09-18 | 2005-01-18 | Aem, Inc. | Dense lead-free glass ceramic for electronic devices |
| KR100444222B1 (en) * | 2001-11-13 | 2004-08-16 | 삼성전기주식회사 | Dielectric Ceramic Compositions |
| JP2004026529A (en) * | 2002-06-21 | 2004-01-29 | Ferro Enamels Japan Ltd | Glass composition for low-temperature fired substrate and glass ceramics using the same |
| TW575535B (en) * | 2003-01-28 | 2004-02-11 | Ruei-Ju Rau | Method for producing high precision multilayered ceramic component |
| DE602005025285D1 (en) * | 2004-06-28 | 2011-01-27 | Tdk Corp | Low temperature simultaneously fired ceramic and multilayer printed circuit board |
| CN102153341B (en) * | 2010-12-07 | 2013-06-05 | 深圳顺络电子股份有限公司 | Medium dielectric constant low-temperature co-fired ceramic material and preparation method thereof |
| KR20160120033A (en) * | 2015-04-07 | 2016-10-17 | 삼성전기주식회사 | Low Temperature Co-Fired Ceramic Substrate And Method of Producing The Same |
| CN110256060B (en) * | 2019-07-09 | 2021-10-08 | 嘉兴佳利电子有限公司 | High-frequency low-dielectric-constant low-temperature co-fired ceramic material and preparation method thereof |
| CN112624617B (en) * | 2020-12-29 | 2021-07-27 | 洛阳中超新材料股份有限公司 | Dielectric constant series adjustable glass powder for low dielectric constant LTCC material and preparation method thereof |
| CN113045204B (en) * | 2021-03-10 | 2023-01-24 | 安徽华封电子科技有限公司 | Low-loss low-temperature co-fired ceramic green tape and preparation method thereof |
| CN113233773B (en) * | 2021-04-28 | 2023-06-16 | 中国电子科技集团公司第四十三研究所 | LTCC substrate material and preparation method thereof |
| CN113372103B (en) * | 2021-07-13 | 2023-01-20 | 中国振华集团云科电子有限公司 | Low-dielectric low-high-frequency-loss LTCC ceramic material and preparation method thereof |
| CN114349493B (en) * | 2022-02-21 | 2022-12-02 | 昆明贵研新材料科技有限公司 | Copper ion doped calcium silicate microwave dielectric ceramic and preparation method thereof |
| CN114644514B (en) * | 2022-03-25 | 2023-03-31 | 上海晶材新材料科技有限公司 | LTCC green tape material, LTCC substrate, LTCF-LTCC heterogeneous substrate and corresponding preparation method |
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Patent Citations (2)
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|---|---|---|---|---|
| CN109467415A (en) * | 2018-11-26 | 2019-03-15 | 中国电子科技集团公司第十三研究所 | The preparation method of low-temperature co-burning ceramic material composite substrate |
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