JPH03257064A - Ceramics for internal chill - Google Patents
Ceramics for internal chillInfo
- Publication number
- JPH03257064A JPH03257064A JP2052370A JP5237090A JPH03257064A JP H03257064 A JPH03257064 A JP H03257064A JP 2052370 A JP2052370 A JP 2052370A JP 5237090 A JP5237090 A JP 5237090A JP H03257064 A JPH03257064 A JP H03257064A
- Authority
- JP
- Japan
- Prior art keywords
- ceramics
- mixture
- sio2
- added
- aluminum titanate
- 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.)
- Pending
Links
- 239000000919 ceramic Substances 0.000 title abstract description 19
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 abstract description 24
- 239000000203 mixture Substances 0.000 abstract description 17
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N Titan oxide Chemical compound O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 abstract description 13
- 235000012239 silicon dioxide Nutrition 0.000 abstract description 12
- 229910052681 coesite Inorganic materials 0.000 abstract description 11
- 229910052906 cristobalite Inorganic materials 0.000 abstract description 11
- 229910052682 stishovite Inorganic materials 0.000 abstract description 11
- 229910052905 tridymite Inorganic materials 0.000 abstract description 11
- 239000000377 silicon dioxide Substances 0.000 abstract description 10
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 abstract description 7
- 238000000465 moulding Methods 0.000 abstract description 7
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 abstract description 6
- 229910052593 corundum Inorganic materials 0.000 abstract description 5
- 238000000034 method Methods 0.000 abstract description 5
- 229910001845 yogo sapphire Inorganic materials 0.000 abstract description 4
- 239000005995 Aluminium silicate Substances 0.000 abstract description 2
- 235000012211 aluminium silicate Nutrition 0.000 abstract description 2
- 238000001125 extrusion Methods 0.000 abstract description 2
- NLYAJNPCOHFWQQ-UHFFFAOYSA-N kaolin Chemical compound O.O.O=[Al]O[Si](=O)O[Si](=O)O[Al]=O NLYAJNPCOHFWQQ-UHFFFAOYSA-N 0.000 abstract description 2
- 239000010453 quartz Substances 0.000 abstract description 2
- 239000000126 substance Substances 0.000 abstract description 2
- 238000004519 manufacturing process Methods 0.000 abstract 1
- 229910000505 Al2TiO5 Inorganic materials 0.000 description 21
- AABBHSMFGKYLKE-SNAWJCMRSA-N propan-2-yl (e)-but-2-enoate Chemical compound C\C=C\C(=O)OC(C)C AABBHSMFGKYLKE-SNAWJCMRSA-N 0.000 description 21
- 238000005266 casting Methods 0.000 description 11
- 230000000694 effects Effects 0.000 description 7
- 230000007423 decrease Effects 0.000 description 6
- 238000005245 sintering Methods 0.000 description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 4
- 239000013078 crystal Substances 0.000 description 4
- 230000035939 shock Effects 0.000 description 4
- 239000000654 additive Substances 0.000 description 3
- 239000012071 phase Substances 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 230000035882 stress Effects 0.000 description 3
- 229910010293 ceramic material Inorganic materials 0.000 description 2
- 238000000354 decomposition reaction Methods 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 239000007791 liquid phase Substances 0.000 description 2
- 238000011068 loading method Methods 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 238000013001 point bending Methods 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- 206010016275 Fear Diseases 0.000 description 1
- MXRIRQGCELJRSN-UHFFFAOYSA-N O.O.O.[Al] Chemical compound O.O.O.[Al] MXRIRQGCELJRSN-UHFFFAOYSA-N 0.000 description 1
- CDBYLPFSWZWCQE-UHFFFAOYSA-L Sodium Carbonate Chemical compound [Na+].[Na+].[O-]C([O-])=O CDBYLPFSWZWCQE-UHFFFAOYSA-L 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 229910001570 bauxite Inorganic materials 0.000 description 1
- LTPBRCUWZOMYOC-UHFFFAOYSA-N beryllium oxide Inorganic materials O=[Be] LTPBRCUWZOMYOC-UHFFFAOYSA-N 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000003054 catalyst Substances 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 230000008602 contraction Effects 0.000 description 1
- 239000010431 corundum Substances 0.000 description 1
- KZHJGOXRZJKJNY-UHFFFAOYSA-N dioxosilane;oxo(oxoalumanyloxy)alumane Chemical compound O=[Si]=O.O=[Si]=O.O=[Al]O[Al]=O.O=[Al]O[Al]=O.O=[Al]O[Al]=O KZHJGOXRZJKJNY-UHFFFAOYSA-N 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- 239000005350 fused silica glass Substances 0.000 description 1
- -1 fused soubirne Chemical compound 0.000 description 1
- 238000001746 injection moulding Methods 0.000 description 1
- YDZQQRWRVYGNER-UHFFFAOYSA-N iron;titanium;trihydrate Chemical compound O.O.O.[Ti].[Fe] YDZQQRWRVYGNER-UHFFFAOYSA-N 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 239000011812 mixed powder Substances 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 229910052863 mullite Inorganic materials 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 238000003303 reheating Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 238000003746 solid phase reaction Methods 0.000 description 1
- 238000010671 solid-state reaction Methods 0.000 description 1
- 230000008646 thermal stress Effects 0.000 description 1
- 239000010936 titanium Substances 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- 238000005303 weighing Methods 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Landscapes
- Compositions Of Oxide Ceramics (AREA)
Abstract
Description
【発明の詳細な説明】 ［産業上の利用分野］ 本発明は鋳ぐるみ用セラミックスに関する。[Detailed description of the invention] [Industrial application field] The present invention relates to ceramics for castings.
［従来の技術］
チタン酸アルミニウムは低熱膨張セラミックスであって
、耐熱衝撃性が高く、しかも融点が１８２０℃と高いの
で、自動車排ガス触媒担体、熱交換体等として用いられ
るほか、自動車エンジンのピストン、シリンダーライナ
、ボートライナ等の餌ぐるみ材料として用いられる。[Prior Art] Aluminum titanate is a low thermal expansion ceramic, has high thermal shock resistance, and has a high melting point of 1820°C, so it is used as an automobile exhaust gas catalyst carrier, a heat exchanger, etc., and is also used as an automobile engine piston, Used as bait material for cylinder liners, boat liners, etc.
チタン酸アルミニウムは熱膨張係数に異方性があり、ａ
軸、ｂ軸およびＣ軸方向でそれぞれ±１１゜８Ｘ１０−
’、＋１９．４Ｘ１０−、−２．６Ｘ１０−６と著しく
大きいものである。このような多結晶体は、焼成後の冷
却時に、その構成結晶粒子の軸方向の収縮または膨張の
差によって、組織中に大きな熱応力が生じ、これが結晶
粒界や粒内にマイクロクラックつまり粒径程度の微細な
亀裂を生ずる。このマイクロクラックは再加熱時にその
間隙が縮まることにより、非常に低い熱膨張を示す。Aluminum titanate has anisotropic thermal expansion coefficient, a
±11° in the axis, b-axis and c-axis directions, respectively 8X10-
', +19.4X10-, -2.6X10-6, which is extremely large. When such a polycrystalline body is cooled after firing, a large thermal stress is generated in the structure due to the difference in axial contraction or expansion of its constituent crystal grains, which causes microcracks or grain formation at grain boundaries and inside the grains. Causes microscopic cracks about the same diameter. These microcracks exhibit very low thermal expansion due to the gaps between them shrinking during reheating.
しかしながら、チタン酸アルミニウムは、１１００〜１
２００℃で分解するため、数％の他の成分（Ｓｉ０２、
Ｆ ｅ２０３、ＢｅＯなと）を加えて固溶体とし、この
分解を抑えている。また、チタン酸アルミニウムだけで
は、強度が著しく低いので、ＳｉＯ２などを添加して強
度を向上する必要がある。However, aluminum titanate has a
Because it decomposes at 200°C, several percent of other components (Si02,
Fe203, BeO, etc.) are added to form a solid solution to suppress this decomposition. Furthermore, since the strength is extremely low when using aluminum titanate alone, it is necessary to add SiO2 or the like to improve the strength.
例えば、特開昭６３−２３６７５９号公報においては、
５ｉｆｔ、Ｍ ｇｏ 、 Ｆ ｅｘ Ｏ３の少なくとも
１種が合計で１０％以下を含有するチタン酸アルミニウ
ムからなる鋳ぐるみ用セラミック材料が開示されている
。For example, in Japanese Patent Application Laid-open No. 63-236759,
A ceramic material for castings made of aluminum titanate containing at least 10% in total of at least one of 5ift, Mgo, and FexO3 is disclosed.
［発明が解決しようとする課題］
しかしながら、鋳ぐるみ用セラミックスは、溶融金属固
化のときの収縮により、大きな圧縮応力が加わるため、
高強度セラミックス材料でも鋳ぐるみ時に部分的に応力
が集中し、破壊してしまうことがあるという問題点があ
る。これは、従来の鋳ぐるみ用セラミックスは、破断歪
が低いことによるものである。[Problems to be Solved by the Invention] However, ceramics for castings are subject to large compressive stress due to shrinkage during solidification of molten metal.
Even high-strength ceramic materials have the problem that stress can be concentrated locally during casting, leading to breakage. This is because conventional casting ceramics have low breaking strain.
例えば、チタン酸アルミニウムを主成分とし、添加剤と
して５ｉｎ２、ＭｇＯ１Ｆｅ２０３等を添加した市販の
錆ぐるみ用セラミックスの破断歪を測定した結果を第３
図に示す、第３図から知られるように、従来から市販の
鋳ぐるみ用チタン酸アルミニウムの破断歪は２０００〜
４０００Ｘ１０”＠ｌ／鋤輪であり、鋳ぐるみ用セラミ
ックスとしては、破断歪が未だ不充分であることが分か
る。For example, the results of measuring the fracture strain of commercially available rust-covering ceramics containing aluminum titanate as the main component and additives such as 5in2, MgO1Fe203, etc.
As shown in Fig. 3, the breaking strain of conventionally commercially available aluminum titanate for castings is 2000~
It can be seen that the fracture strain is still insufficient for ceramics for castings.
本発明は従来の鋳ぐるみ用セラミックスであるチタン酸
アルミニウムの破断歪が低いため、ボートライナなどと
して鋳ぐるんだ時に溶湯の凝固の際の圧縮応力により破
壊してしまうという問題点を解決すべくなされたもので
あって、破断歪を著しく改善した銃ぐるみ用セラミック
スを提供することを目的とする。The present invention aims to solve the problem that aluminum titanate, which is a conventional casting ceramic, has a low breaking strain, so when it is cast as a boat liner, etc., it breaks due to compressive stress during solidification of molten metal. The object of the present invention is to provide ceramics for gun housings which have significantly improved fracture strain.
［課題を解決するための手段］
本発明の鋳ぐるみ用セラミックスは、重量比で、Ａ Ｌ
Ｏｙ：４０〜６５ Ｘ、ＴｉＯ２；３０〜６０％、Ｓ
ｉ Ｏ２； ２ 、 Ｏ〜５ 、５％、Ｆｅ２Ｏ＊：２
．０〜３．０％を含有し、破断歪が３０００〜１００Ｏ
ＯＸＩＱ−’＋ｕｅ／ｗｎであることを要旨とする。[Means for Solving the Problems] The casting ceramics of the present invention has a weight ratio of A L
Oy: 40-65X, TiO2; 30-60%, S
i O2; 2, O~5, 5%, Fe2O*:2
．． Contains 0-3.0% and has a breaking strain of 3000-100O
The gist is that OXIQ-'+ue/wn.
本発明のチタン酸アルミニウムを製造するには、まずア
ルミナ、ローソーダアルミナ、仮焼ボーキサイト、精製
ルチル、粗製ルチル、アナターゼ型チタン、イルメナイ
ト、フェライトベンガラ、電融スビルネ、カオリン、石
英、電融シリカ等から化学組成が酸化物換算した重量比
でＡ Ｉ２０３；４０〜６５％、Ｔ ｉｏ ｚ；３０〜
６０％、Ｓ ｉ Ｏ２； ２ 、０〜５．５％、Ｆ ｅ
２０ ｓ ： ２ 、０〜３ 、０％になるように原
料を選択し混合物を得る。混合物には必要に応じ成形助
剤を加え、押出成形法、プレス成形法、スリップキャス
ト成形法、射出成形法などのセラミックス成形法により
成形後乾燥する。To produce the aluminum titanate of the present invention, first, alumina, low soda alumina, calcined bauxite, purified rutile, crude rutile, anatase type titanium, ilmenite, ferrite red iron, fused soubirne, kaolin, quartz, fused silica, etc. The chemical composition is A I203; 40-65%, Tio z; 30-65% in terms of weight ratio in terms of oxide.
60%, SiO2; 2, 0-5.5%, Fe
20s: Select the raw materials so that the ratio is 2.0 to 3.0% to obtain a mixture. A molding aid is added to the mixture if necessary, and the mixture is molded by a ceramic molding method such as an extrusion molding method, a press molding method, a slip cast molding method, or an injection molding method, and then dried.
なお、本発明のセラミックスの成分組成の限定理由は次
の通りである。The reasons for limiting the component composition of the ceramic of the present invention are as follows.
Ａ Ｉ２０３；４０〜５０ ％、Ｔ ｉ Ｏ２； ３０
〜６０％Ａ Ｉ２０３およびＴ ｉ Ｏ２からは固体反
応により、チタン酸アルミニウムが合成される。Ａｌ２
Ｏ＊またはＴｉＯ２の添加量がこの組成範囲未満である
と、チタン酸アルミニウムの結晶量が充分に確保できず
、熱膨張係数が２０ Ｘ １０−’／”Ｃ以下とならな
い、また、ＡＬＯｉまたはＴ ｉ Ｏ２の添加量がこの
組成範囲を越えると、Ａｌ２Ｏ３またはＴ ｉ Ｏ２が
過剰になって、熱膨張係数が急激に増加する。A I203; 40-50%, T i O2; 30
~60% Aluminum titanate is synthesized from A I203 and T i O2 by a solid-state reaction. Al2
If the amount of O* or TiO2 added is less than this composition range, a sufficient amount of aluminum titanate crystals cannot be secured, and the coefficient of thermal expansion will not be less than 20 x 10-'/''C. When the amount of i O2 added exceeds this composition range, Al2O3 or T i O2 becomes excessive and the coefficient of thermal expansion sharply increases.
Ｆ ｅｚｏ ３；２．０〜３．０％
Ｆｅ２Ｏ３はチタン酸アルミニウムに固溶することによ
り、合成されたチタン酸アルミニウムの１１００〜１２
００℃における分解を抑制するために添加される。また
、チタン酸アルミニウムの破断歪を向上させる効果があ
る。Ｆｅ２ｕ３が２．０％未満であると、前記効果が不
充分であり、熱膨張係数の変化を防止することができな
い、Ｆｅ２ｒｓの添加量が３．０％を越えると、融点が
低下し熱膨張係数が増加して、耐熱衝撃性が低下すとと
もに、破断歪が逆に低下する。Fezo 3; 2.0 to 3.0% Fe2O3 is dissolved in aluminum titanate as a solid solution to give 1100 to 12% of the synthesized aluminum titanate.
Added to suppress decomposition at 00°C. It also has the effect of improving the breaking strain of aluminum titanate. If Fe2u3 is less than 2.0%, the above effect is insufficient and changes in the coefficient of thermal expansion cannot be prevented. If the amount of Fe2rs added exceeds 3.0%, the melting point decreases and thermal expansion decreases. As the coefficient increases, the thermal shock resistance decreases, and the breaking strain conversely decreases.
Ｓ ｉｏ２；２．０〜５．５％
ＳｉＯ２はチタン酸アルミニウムの強度および破断歪を
向上させるために添加する。添加量が２０％未満である
と、強度および破断歪を向上させる効果が不充分である
。また、Ｓ ｉ Ｏ２の添加量が５．５％を越えると、
強度の向上の効果が飽和するとともに、破断歪が低下す
るので上限を５．５％とした。S io2; 2.0 to 5.5% SiO2 is added to improve the strength and breaking strain of aluminum titanate. If the amount added is less than 20%, the effect of improving strength and breaking strain will be insufficient. Moreover, when the amount of S i O2 added exceeds 5.5%,
The upper limit was set at 5.5% since the effect of improving strength is saturated and the breaking strain is reduced.
得られた成形体は１４２０〜１４８０℃で５時間以上保
持して合成される。成形体の保持温度を１４２０〜１４
８０℃にしたのは、保持温度が１４２０℃未渭であると
、添加剤の活量が低く、チタン酸アルミニウムとの固溶
体が生成しないからであり、１４８０℃を越えると、液
相が増加してＦｅ２０ａから分解した０２ガスが系から
逸散しないからである。また、保持時間を５時間以上と
したのは、５時間未満であると、液相から０２ガスが充
分に発散しないからである。The obtained molded body is synthesized by maintaining it at 1420 to 1480°C for 5 hours or more. The holding temperature of the molded body is 1420-14
The reason why the holding temperature was set at 80°C is because if the holding temperature is not left at 1420°C, the activity of the additive will be low and a solid solution with aluminum titanate will not be formed.If it exceeds 1480°C, the liquid phase will increase. This is because the 02 gas decomposed from Fe20a does not escape from the system. Further, the reason why the holding time is set to 5 hours or more is because if the holding time is less than 5 hours, the 02 gas will not be sufficiently released from the liquid phase.
この成形体は焼結温度を１５００〜１６００℃として焼
結される。１５００℃未満では焼結が充分に進行せず、
かつ結晶粒子が充分に成長せず熱膨張係数が高くなるか
らであり、１６００℃を越えると圧縮強度が低下し耐熱
衝撃性が低下するからである。また、焼結時間は、１時
間未満では、焼結が完了せず、１０時間でほぼ焼結が完
了する。This molded body is sintered at a sintering temperature of 1500 to 1600°C. Sintering does not proceed sufficiently below 1500°C,
This is also because the crystal grains do not grow sufficiently and the thermal expansion coefficient becomes high, and when the temperature exceeds 1600°C, the compressive strength decreases and the thermal shock resistance decreases. Further, if the sintering time is less than 1 hour, the sintering will not be completed, and the sintering will be almost completed in 10 hours.
かくして得られた焼結体は、チタン酸アルミニウムの結
晶相を６５％以上含有し、破断歪が３０００〜１００Ｏ
ＯＸＩＯ−・■／−鋤となる。また、得られた焼結体に
は、チタン酸アルミニウム以外の第２の結晶相として、
ルチル、コランダム、ムライト等の少なくとも１種を含
有しても差し支えない。The sintered body thus obtained contains 65% or more of aluminum titanate crystal phase and has a breaking strain of 3000 to 100O.
OXIO-・■/-becomes a plow. The obtained sintered body also contained a second crystalline phase other than aluminum titanate.
It may contain at least one of rutile, corundum, mullite, and the like.
［実施例コ
本発明の実施例を比較例とともに説明し、本発明の効果
を明らかにする。[Example] Examples of the present invention will be explained together with comparative examples to clarify the effects of the present invention.
Ａ ｌ ２０３ トＴ ！ ０２が等モル比（重量比で
５６．１４３．９）となるように原料を秤量した混合粉
末に、添加剤として第１表に示す重量％のＳｉＯ２粉末
およびＦｅ２Ｏ３を加え、さらにこの調合物に適量の結
合剤加え、十分に混合した後、１０００ ｋｇ／ ｃｍ
２の圧力で１０＋ｍ＋ｓＸ Ｉ Ｃ）＋ｎＸ ８０＋＋
ｎの成形体を調製した。A l 203 ToT! SiO2 powder and Fe2O3 in the weight percent shown in Table 1 were added as additives to a mixed powder prepared by weighing the raw materials so that the molar ratio of 02 to After adding appropriate amount of binder and mixing thoroughly, 1000 kg/cm
10+m+sX I C)+nX 80++ at a pressure of 2
A molded body of n was prepared.
なお、第１表において番号１〜６は、Ｆｅ２Ｏ。In addition, numbers 1 to 6 in Table 1 are Fe2O.
の添加量を２６５％に固定し、Ｓ ｉ Ｏ２添加量を１
゜０％から６，０％まで変化させたものであり、番号７
〜１２は、ＳｉＯ□添加量を２．５％に固定し、Ｆｅ２
ｅ３添加量を１．０％から４．０％まで変化させたもの
であり、番号１３はＦｅ２ｅｓおよび５ｉＯ１をそれぞ
れ１．５％つづ添加したものである。The amount of S i O2 added was fixed at 265%, and the amount of S i O2 added was set to 1.
゜It is changed from 0% to 6,0%, and number 7
~12, the amount of SiO□ added was fixed at 2.5%, and Fe2
The amount of e3 added was varied from 1.0% to 4.0%, and number 13 was one in which 1.5% each of Fe2es and 5iO1 was added.
得られた成形体を１４５０℃で５時間加熱保持してチタ
ン酸アルミニウムを合成した後、１５５０℃で１０時間
加熱焼結して、焼結体を得た。得られた焼結体について
、破断歪、強度および熱膨張係数を測定した。The obtained molded body was heated and held at 1450° C. for 5 hours to synthesize aluminum titanate, and then heated and sintered at 1550° C. for 10 hours to obtain a sintered body. The fracture strain, strength, and thermal expansion coefficient of the obtained sintered body were measured.
破断歪については、焼結体から幅４−膳、厚さ３１、長
さ４５＋ｅｍの試験片を切り出し、内側スパン１０ｍ蒙
、外側スパン３０ＩＩＩ１１、荷重速度０．５＋＊ｍ／
分の条件で４点曲げ試験を行い、負荷点の移動量を試験
片のたわみ量として、計算して求めた。Regarding the breaking strain, a test piece with a width of 4 mm, a thickness of 31 mm, and a length of 45 + em was cut from the sintered body, and the inner span was 10 mm, the outer span was 30 mm, and the loading rate was 0.5 + * m/.
A 4-point bending test was conducted under the conditions of 100 to 200 mL, and the amount of movement of the load point was calculated as the amount of deflection of the test piece.
強度については、焼結体から幅４鵠納、厚さ３ＭＩｍ、
長さ４５ｍ−の試験片を切り出し、内側スパン１０−１
外側スパン３０ＩＩＩＩ、荷重速度０．５＋＊ｍ／分の
条件で４点曲げ強度の測定を行い、計算式によって求め
た。Regarding strength, the width of the sintered body is 4 mm, the thickness is 3 MIm,
A test piece with a length of 45 m was cut out, and the inner span was 10-1.
Four-point bending strength was measured under the conditions of an outer span of 30III and a loading rate of 0.5+*m/min, and was determined using a calculation formula.
熱膨張係数については、押棒式の熱膨張計を用い、１０
００℃までの熱膨張を測定して求めた。For the coefficient of thermal expansion, a push rod type thermal dilatometer was used, and 10
It was determined by measuring thermal expansion up to 00°C.
なお、第２相については、Ｘ線回折法により測定し、ピ
ークの値から同定して求めた。The second phase was measured by X-ray diffraction and identified from the peak value.
得られた結果は第１表に併せて示した。また、Ｓ ｉ
Ｏ２またはＦｅｚＯ＊の添加量と破断歪の関係を示す線
区を第１図および第２図に示した。The obtained results are also shown in Table 1. Also, S i
Lines showing the relationship between the amount of O2 or FezO* added and the breaking strain are shown in FIGS. 1 and 2.
（以下余白）
第１表および第１図に示したように、５１０２が２．０
％未満である場合およびＳｉＯ２が５．５％を越える場
合は、破断歪が２０００Ｘ１０−’ｓ＋＊／■以下であ
るが、Ｓ ｉ Ｏ２が本発明の組成範囲である２、０〜
５．５％において、破断歪が７０００Ｘ １０−’１１
１１／ ＠−以上となり、破断歪が著しく改善されるこ
とが確認された。また、本発明の組成範囲において、強
度は８〜１５ＭＰａであって、十分な強度を有し、かつ
熱膨張係数が−０，５〜２゜０ＸＩＯ−’／”Ｃであっ
て、十分な耐熱衝撃性を有することが明らかとなった。(Left below) As shown in Table 1 and Figure 1, 5102 is 2.0
% and when SiO2 exceeds 5.5%, the breaking strain is 2000X10-'s+*/■ or less, but when SiO2 is within the composition range of the present invention,
At 5.5%, the breaking strain is 7000X 10-'11
11/@- or more, and it was confirmed that the breaking strain was significantly improved. Further, in the composition range of the present invention, the strength is 8 to 15 MPa, which is sufficient strength, and the coefficient of thermal expansion is -0.5 to 2°0XIO-'/''C, which has sufficient heat resistance. It was revealed that it has impact resistance.
また、第１表と第２図から知られるように、Ｆｅ２Ｏ，
が２．０％未満である場合およびＦｅａｒｓが３．０％
を越える場合は、破断歪が２０００Ｘ１０−’＋ｕｅ／
−輪以下であるが、Ｆｅ２Ｏ３が本発明の組成範囲であ
る２、０〜３．０％において、破断歪が７０００Ｘ１０
−’輸−／輸−以上となり、破断歪が著しく改善される
ことが確認された。また、本発明の組成範囲において、
強度は７〜１０ＭＰａであって、十分な強度を有し、か
つ熱膨張係数が０〜２．ＯＸｌ ０−’／”Ｃであって
、十分な耐熱衝撃性を有することが明らかとなった。Also, as is known from Table 1 and Figure 2, Fe2O,
is less than 2.0% and Fears is 3.0%
If the breaking strain exceeds 2000X10-'+ue/
- However, when Fe2O3 is in the composition range of the present invention of 2.0 to 3.0%, the breaking strain is 7000X10.
It was confirmed that the fracture strain was significantly improved. Moreover, in the composition range of the present invention,
The strength is 7 to 10 MPa, which is sufficient strength, and the coefficient of thermal expansion is 0 to 2. OXl 0-'/''C, and was found to have sufficient thermal shock resistance.
なお、ＳｉＯ２およびＦ ｅ２０３をそれぞれ１．５％
しか含有しない番号１３は、熱膨張係数は低いものの、
強度および破断歪が著しく低かった。In addition, SiO2 and Fe203 were each 1.5%
Number 13, which contains only
The strength and strain at break were significantly lower.
［発明の効果コ
本発明の鋳ぐるみ用ラセミックスは、以上説明したよう
に、重量比で、Ａｌ２Ｏ３；４０〜６５％、Ｔ １ｏｌ
ａ；３０〜６０％、Ｓ ｉ Ｏ２； ２ 、 Ｏ〜５
、５％、Ｆｅ２０ｓ；２．０〜３．０％を含有するもの
であって、合成されたチタン酸アルミニウムに破断歪が
著しく改善される組成範囲のＳ ｒ ０２およびＦ ｅ
２０ ａを含有せしめたので、破断歪が３０００〜１０
０００ Ｘ １０−’ｓｉｓ／ ｗ＋＊に改善され、エ
ンジンのポートライナやシリンダライナ等の鋳ぐるみ用
セラミックスとして極めて有用である。[Effects of the Invention] As explained above, the racemic for castings of the present invention contains Al2O3; 40 to 65%, T 1ol, in terms of weight ratio.
a; 30-60%, SiO2; 2, O-5
, 5%, Fe20s; 2.0 to 3.0%, S r 02 and Fe 20s in a composition range that significantly improves the breaking strain of the synthesized aluminum titanate.
Since it contains 20 a, the breaking strain is 3000~10
000 x 10-'sis/w+*, and is extremely useful as a ceramic for castings such as engine port liners and cylinder liners.
第１図は５ｉｎ２の添加量と破断歪の間係を示す線図、
第２図はＦ ｅ２０ ｖの添加量と破断歪の関係を示す
線図、第３図は従来から市販されているチタン酸アルミ
ニウ五の破断歪を示す棒グラフである。Figure 1 is a diagram showing the relationship between the addition amount of 5in2 and the breaking strain,
FIG. 2 is a diagram showing the relationship between the amount of F e20 v added and the breaking strain, and FIG. 3 is a bar graph showing the breaking strain of conventionally commercially available aluminum titanate.
Claims (1)
Ｏ＿２；３０〜６０％、ＳｉＯ＿２；２．０〜５．５％
、Ｆｅ＿２Ｏ＿３；２．０〜３．０％を含有し、破断歪
が３０００〜１００００×１０＾−＾６ｍｍ／ｍｍであ
ることを特徴とする鋳ぐるみ用セラミックス。(1) Weight ratio: Al_2O_3; 40-65%, Ti
O_2; 30-60%, SiO_2; 2.0-5.5%
, Fe_2O_3; 2.0 to 3.0%, and a breaking strain of 3000 to 10000×10^-^6 mm/mm.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2052370A JPH03257064A (en) | 1990-03-02 | 1990-03-02 | Ceramics for internal chill |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2052370A JPH03257064A (en) | 1990-03-02 | 1990-03-02 | Ceramics for internal chill |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH03257064A true JPH03257064A (en) | 1991-11-15 |
Family
ID=12912923
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2052370A Pending JPH03257064A (en) | 1990-03-02 | 1990-03-02 | Ceramics for internal chill |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH03257064A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105153724A (en) * | 2015-08-31 | 2015-12-16 | 苏州莱特复合材料有限公司 | Iron-based composite material for cylinder liners and method for manufacturing iron-based composite material |
-
1990
- 1990-03-02 JP JP2052370A patent/JPH03257064A/en active Pending
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105153724A (en) * | 2015-08-31 | 2015-12-16 | 苏州莱特复合材料有限公司 | Iron-based composite material for cylinder liners and method for manufacturing iron-based composite material |
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