JPH026999B2 - - Google Patents
Info
- Publication number
- JPH026999B2 JPH026999B2 JP15776482A JP15776482A JPH026999B2 JP H026999 B2 JPH026999 B2 JP H026999B2 JP 15776482 A JP15776482 A JP 15776482A JP 15776482 A JP15776482 A JP 15776482A JP H026999 B2 JPH026999 B2 JP H026999B2
- Authority
- JP
- Japan
- Prior art keywords
- silicon carbide
- weight
- heat exchanger
- oxidation
- terms
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired
Links
- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 claims description 25
- 229910010271 silicon carbide Inorganic materials 0.000 claims description 21
- 229910052751 metal Inorganic materials 0.000 claims description 5
- 239000002184 metal Substances 0.000 claims description 5
- 239000012530 fluid Substances 0.000 claims description 4
- 238000005192 partition Methods 0.000 claims description 4
- 229910052796 boron Inorganic materials 0.000 claims description 3
- 238000005229 chemical vapour deposition Methods 0.000 claims description 3
- 239000000463 material Substances 0.000 claims description 3
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims description 2
- 238000007254 oxidation reaction Methods 0.000 description 10
- 230000003647 oxidation Effects 0.000 description 9
- 229910004298 SiO 2 Inorganic materials 0.000 description 6
- 238000005245 sintering Methods 0.000 description 4
- 239000011248 coating agent Substances 0.000 description 3
- 238000000576 coating method Methods 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 150000002739 metals Chemical class 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 230000000704 physical effect Effects 0.000 description 2
- 239000011148 porous material Substances 0.000 description 2
- 239000000843 powder Substances 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910000881 Cu alloy Inorganic materials 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 229910021431 alpha silicon carbide Inorganic materials 0.000 description 1
- 239000012752 auxiliary agent Substances 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 239000000919 ceramic Substances 0.000 description 1
- 229910010293 ceramic material Inorganic materials 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 229910052878 cordierite Inorganic materials 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- JSKIRARMQDRGJZ-UHFFFAOYSA-N dimagnesium dioxido-bis[(1-oxido-3-oxo-2,4,6,8,9-pentaoxa-1,3-disila-5,7-dialuminabicyclo[3.3.1]nonan-7-yl)oxy]silane Chemical compound [Mg++].[Mg++].[O-][Si]([O-])(O[Al]1O[Al]2O[Si](=O)O[Si]([O-])(O1)O2)O[Al]1O[Al]2O[Si](=O)O[Si]([O-])(O1)O2 JSKIRARMQDRGJZ-UHFFFAOYSA-N 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- 229910000856 hastalloy Inorganic materials 0.000 description 1
- 238000005338 heat storage Methods 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 229910001026 inconel Inorganic materials 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 239000005011 phenolic resin Substances 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
Classifications
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F28—HEAT EXCHANGE IN GENERAL
- F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
- F28F21/00—Constructions of heat-exchange apparatus characterised by the selection of particular materials
- F28F21/04—Constructions of heat-exchange apparatus characterised by the selection of particular materials of ceramic; of concrete; of natural stone
Landscapes
- Engineering & Computer Science (AREA)
- Ceramic Engineering (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Mechanical Engineering (AREA)
- General Engineering & Computer Science (AREA)
Description
本発明は炭化珪素からなる熱交換器の改良にな
るものである。熱交換器は高温の流体の保有する
熱を隔壁を介して低温の流体を加熱するものであ
るため、隔壁を構成する部材には熱伝導の良好な
ものが使用される。この場合、低温用には銅、銅
合金が使用されることが多いが1000℃以下程度の
温度の場合にはインコネル、ハステロイ等の耐熱
金属が使用される。又、1000℃を越える高温で
は、金属材料は耐蝕性が極端に低下し、ほとんど
使用できない。このため炭素、炭化珪素、コージ
ライト等のセラミツクス材料の使用が考えられる
が、セラミツクは加工性、信頼性に乏しく複雑な
形状のものは得られない。例えば、炭化珪素は本
質的には耐酸化性のある材料であるが、従来の粘
土結合したような炭化珪素では特に高温における
荷重軟化に弱く、又、形成されたSiO2被膜が変
質し、SiO2の形成と共に内部と表面部との応力
の差が次第に増大し、ついには被膜が剥離する等
持てる特性を充分に発揮し得ない状態であつた。
本発明は炭化珪素の持つ特性を充分生かすべ
く、その欠点を究明し、これを改善することによ
つて従来に見られないすぐれた熱交換器を開発し
たもので、炭化珪素をホウ素成分及びAl、Be、
Mg、Ti等の焼結助剤を使用して焼結炭化珪素と
したものである。
即ち、炭化珪素の酸化は炭化珪素自体が酸化さ
れ、その表面にSiO2被膜が形成され、このSiO2
の被膜が剥離すると新に露出した炭化珪素が酸化
を受けるという過程で進行する。この場合、生成
したSiO2被膜が剥離することなく存在すれば、
炭化珪素の酸化は停止するが、このSiO2被膜は
Fe2O3、Na2O等の不純物が存在すると熱的に不
安定な組成に転化し、SiO2の被膜の剥離につな
がることが明らかとなつた。しかも、この現象は
成形体の表面のみでなく気孔を介して内部に迄酸
化が拡散するので気孔の存在状態も耐酸化性に大
きな影響を与える。
従つて、本発明のものにおいては炭化珪素成形
体自体を緻密化することによつて酸化を表面部の
みに特定し、もつて長寿命化をはかつたもので、
緻密化させるためには炭化珪素紛の焼結に際し、
ホウ素成分をBに換算して0.05〜5.50重量%を加
えたもので、これを更に焼結晶の熱伝導性を改善
するために、金属に換算してAl、Be、Mg、Ti
のうち少なくとも一成分を0.05〜5.50重量%添加
するものである。
即ち、ホウ素成分及びAl、Be、Mg、Ti等の
成分の少なくとも一種をそれぞれ0.05〜5.50重量
%を焼結助剤として添加した炭化珪素紛を成形焼
成することによつて炭化珪素紛が自己焼結し、粒
界のきわめて少ない緻密な成形体となるため、熱
的、化学的に炭化珪素より特性の劣る部分が実質
的に存在せず、結局酸化反応は成形体の表面層の
みに限定されることになる。これが成形体の寿命
延長に寄与し、かつ高熱伝導率を有する焼結体と
なるものである。
本発明において、Bを添加するのはサブミクロ
ンのSiC紛末を焼結するための助剤とするため
で、この割合を逸脱するとガス不透過性の緻密な
焼結体が得られない。又、金属でも酸化物でもよ
いが金属に換算してAl、Be、Mg、Tiのうち少
なくとも一つの成分を添加するのは、Bで自己焼
結させた炭化珪素成形体の熱伝導性を改善するた
めのものであり、0.05重量%以下ではその効果が
ほとんど認められず、又、5.50重量%以上では焼
結性に悪影響を及ぼし緻密なものとなりにくいば
かりでなく、焼結体の粒界部分に存在するこれら
添加物は炭化珪素粒子の部分と比較して侵蝕を受
け易く、結局耐蝕性のある焼結体とはなりにく
い。
以下に本発明の実施例につき説明する。
平均粒径0.5μのα−SiC紛末にBを2.5重量%及
びBeを2.5重量%となるように配合し、フエノー
ルレジン2重量%を一次結合剤として混合成形
し、これを2050℃で焼結することによつて嵩比重
3.13g/c.c.、熱伝導率200w/m.kの物性を有する
ものであつた。これは従来のBe無添加の焼結体
と比較して約4倍の熱伝導率を示すものである。
この試料を空気中1250℃に加熱して酸化による
クラツク発生までの寿命測定を行なつた所、88日
であつた。
比較のためBeの添加割合のみを変えた試料を
作成し、その物性を以下の表に示す。
The present invention is an improvement on a heat exchanger made of silicon carbide. Since the heat exchanger heats the low-temperature fluid by using the heat held by the high-temperature fluid through the partition walls, materials with good heat conductivity are used for the members forming the partition walls. In this case, copper and copper alloys are often used for low temperatures, but heat-resistant metals such as Inconel and Hastelloy are used for temperatures below 1000°C. Furthermore, at high temperatures exceeding 1000°C, the corrosion resistance of metal materials is extremely reduced, making them almost unusable. For this reason, it is possible to use ceramic materials such as carbon, silicon carbide, and cordierite, but ceramics have poor workability and reliability, and complex shapes cannot be obtained. For example, silicon carbide is essentially an oxidation-resistant material, but conventional clay-bonded silicon carbide is particularly susceptible to softening under load at high temperatures, and the formed SiO 2 film changes in quality, resulting in SiO With the formation of No. 2 , the difference in stress between the inside and the surface gradually increased, and eventually the coating peeled off, making it impossible to fully demonstrate its properties. In order to make full use of the characteristics of silicon carbide, the present invention has investigated its shortcomings and improved them to develop an excellent heat exchanger that has never been seen before. ,Be,
Sintered silicon carbide is made using sintering aids such as Mg and Ti. That is, in the oxidation of silicon carbide, silicon carbide itself is oxidized, a SiO 2 film is formed on its surface, and this SiO 2
When the coating peels off, the newly exposed silicon carbide undergoes oxidation. In this case, if the generated SiO 2 film exists without peeling off,
Oxidation of silicon carbide stops, but this SiO 2 film
It has become clear that the presence of impurities such as Fe 2 O 3 and Na 2 O transforms the composition into a thermally unstable composition, leading to peeling of the SiO 2 film. In addition, this phenomenon causes oxidation to diffuse not only to the surface of the molded product but also to the inside through the pores, so the state of the pores also has a great effect on the oxidation resistance. Therefore, in the present invention, by making the silicon carbide molded body itself dense, oxidation is limited to only the surface area, thereby extending the life of the product.
In order to make it dense, when sintering silicon carbide powder,
0.05 to 5.50% by weight of boron is added in terms of B, and in order to further improve the thermal conductivity of the fired crystal, it is added to Al, Be, Mg, Ti in terms of metals.
At least one component is added in an amount of 0.05 to 5.50% by weight. That is, silicon carbide powder is self-sintered by molding and firing silicon carbide powder to which 0.05 to 5.50% by weight of each of at least one of Al, Be, Mg, and Ti is added as a sintering aid. This results in a dense compact with very few grain boundaries, so there is virtually no part with thermally or chemically inferior properties to silicon carbide, and the oxidation reaction is ultimately limited to the surface layer of the compact. That will happen. This contributes to extending the life of the molded body and results in a sintered body having high thermal conductivity. In the present invention, B is added to serve as an auxiliary agent for sintering submicron SiC powder, and if the proportion is outside this range, a dense sintered body that is gas-impermeable cannot be obtained. In addition, adding at least one component among Al, Be, Mg, and Ti, which may be a metal or an oxide, in terms of metal improves the thermal conductivity of the silicon carbide molded body self-sintered with B. If it is less than 0.05% by weight, almost no effect will be observed, and if it is more than 5.50% by weight, it will not only adversely affect the sinterability and make it difficult to form a dense product, but also reduce the grain boundary area of the sintered body. These additives present in the silicon carbide particles are more susceptible to corrosion than the silicon carbide particles, and as a result, it is difficult to form a corrosion-resistant sintered body. Examples of the present invention will be described below. 2.5% by weight of B and 2.5% by weight of Be were blended into α-SiC powder with an average particle size of 0.5μ, mixed and molded with 2% by weight of phenol resin as a primary binder, and this was sintered at 2050°C. By tying the bulk density
It had physical properties of 3.13g/cc and thermal conductivity of 200w/mk. This shows a thermal conductivity approximately four times higher than that of a conventional sintered body without the addition of Be. This sample was heated to 1250°C in air to measure its lifespan until cracks occurred due to oxidation, and it was 88 days. For comparison, samples were prepared in which only the addition ratio of Be was changed, and their physical properties are shown in the table below.
【表】
表において寿命(日)はクラツクの発生が目視
されるまでの日数である。
又、Beに変えてAl、Mg、Tiについても比較
試験を行つたがほゞ同等の結果が得られた。
本発明によつて期待できる効果は、二重管式の
みならず、多管式のもの、或いは自動車用等のガ
スタービンエンジンの蓄熱式、伝熱式等のものへ
の応用が可能である。
又、本発明の焼結体表面に更にCVD(化学蒸着
法)によつて炭化珪素膜をコーテイングしたもの
は、その被覆が緻密にかつ強固に形成されている
ため耐酸化性が更に向上し寿命の延長をはかるこ
とができる。[Table] In the table, lifespan (days) is the number of days until cracks are visually observed. Comparative tests were also conducted on Al, Mg, and Ti instead of Be, and almost the same results were obtained. The effects that can be expected from the present invention can be applied not only to double-tube type engines, but also to multi-tube types, or heat storage type, heat transfer type, etc. of gas turbine engines for automobiles. Furthermore, in the case of the sintered body of the present invention, which is further coated with a silicon carbide film by CVD (chemical vapor deposition), the coating is formed densely and firmly, which further improves oxidation resistance and extends the lifespan. can be extended.
Claims (1)
熱する方式の熱交換器において、該隔壁の少なく
とも一部が炭化珪素粉に対し、ホウ素成分をBに
換算して0.05〜5.50重量%及び金属に換算して
Al、Be、Mg、Tiのうち少なくとも一成分を0.05
〜5.50重量%含む焼結炭化珪素質材料を用いるこ
とを特徴とする炭化珪素質熱交換器。 2 少なくとも表面の一部にCVD法による炭化
珪素膜が被覆されていることを特徴とする特許請
求の範囲第1項記載の炭化珪素質熱交換器。[Claims] 1. In a heat exchanger that heats a low-temperature fluid with a high-temperature fluid through a partition wall, at least a portion of the partition wall contains silicon carbide powder with a boron component of 0.05 in terms of B. ~5.50% by weight and in terms of metal
At least one component among Al, Be, Mg, and Ti is 0.05%
A silicon carbide heat exchanger characterized by using a sintered silicon carbide material containing ~5.50% by weight. 2. The silicon carbide heat exchanger according to claim 1, wherein at least a part of the surface is coated with a silicon carbide film formed by a CVD method.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP15776482A JPS5946493A (en) | 1982-09-10 | 1982-09-10 | Heat exchanger of silicon carbide material |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP15776482A JPS5946493A (en) | 1982-09-10 | 1982-09-10 | Heat exchanger of silicon carbide material |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS5946493A JPS5946493A (en) | 1984-03-15 |
JPH026999B2 true JPH026999B2 (en) | 1990-02-14 |
Family
ID=15656799
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP15776482A Granted JPS5946493A (en) | 1982-09-10 | 1982-09-10 | Heat exchanger of silicon carbide material |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS5946493A (en) |
Families Citing this family (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US5260056A (en) * | 1988-11-15 | 1993-11-09 | Sanwa Kagaku Kenkyusho Co. Ltd. | Composition for enhancing biosynthesis of interferon |
EP3326988B1 (en) * | 2015-08-28 | 2019-11-06 | Kyocera Corporation | Flow path member |
-
1982
- 1982-09-10 JP JP15776482A patent/JPS5946493A/en active Granted
Also Published As
Publication number | Publication date |
---|---|
JPS5946493A (en) | 1984-03-15 |
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