JPS61207566A - Formation of thermally sprayed ceramic film - Google Patents
Formation of thermally sprayed ceramic filmInfo
- Publication number
- JPS61207566A JPS61207566A JP60047400A JP4740085A JPS61207566A JP S61207566 A JPS61207566 A JP S61207566A JP 60047400 A JP60047400 A JP 60047400A JP 4740085 A JP4740085 A JP 4740085A JP S61207566 A JPS61207566 A JP S61207566A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- thermal
- base material
- sprayed
- thermally sprayed
- 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.)
- Granted
Links
- 239000000919 ceramic Substances 0.000 title claims abstract description 10
- 230000015572 biosynthetic process Effects 0.000 title abstract 2
- 239000000463 material Substances 0.000 claims abstract description 39
- 238000005507 spraying Methods 0.000 claims abstract description 19
- 238000000034 method Methods 0.000 claims abstract description 12
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 7
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 5
- 229910000838 Al alloy Inorganic materials 0.000 claims abstract 4
- 238000007751 thermal spraying Methods 0.000 claims description 9
- 229910010293 ceramic material Inorganic materials 0.000 claims description 6
- 239000011651 chromium Substances 0.000 claims description 5
- 229910002076 stabilized zirconia Inorganic materials 0.000 claims description 5
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 4
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 3
- -1 nickel-chromium-aluminum Chemical compound 0.000 claims description 2
- NPXOKRUENSOPAO-UHFFFAOYSA-N Raney nickel Chemical compound [Al].[Ni] NPXOKRUENSOPAO-UHFFFAOYSA-N 0.000 claims 1
- 229910000623 nickel–chromium alloy Inorganic materials 0.000 claims 1
- 229910045601 alloy Inorganic materials 0.000 abstract description 28
- 239000000956 alloy Substances 0.000 abstract description 28
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 abstract description 20
- 229910018487 Ni—Cr Inorganic materials 0.000 abstract description 10
- 238000002485 combustion reaction Methods 0.000 abstract description 3
- 230000007797 corrosion Effects 0.000 abstract description 2
- 238000005260 corrosion Methods 0.000 abstract description 2
- 229910003310 Ni-Al Inorganic materials 0.000 abstract 2
- 229910002061 Ni-Cr-Al alloy Inorganic materials 0.000 abstract 1
- 238000012360 testing method Methods 0.000 description 12
- 238000000576 coating method Methods 0.000 description 11
- 239000011248 coating agent Substances 0.000 description 10
- 238000010438 heat treatment Methods 0.000 description 9
- 230000000694 effects Effects 0.000 description 7
- 239000000843 powder Substances 0.000 description 6
- 239000007921 spray Substances 0.000 description 6
- 230000000052 comparative effect Effects 0.000 description 3
- 238000009864 tensile test Methods 0.000 description 3
- 229910000599 Cr alloy Inorganic materials 0.000 description 2
- CPLXHLVBOLITMK-UHFFFAOYSA-N Magnesium oxide Chemical compound [Mg]=O CPLXHLVBOLITMK-UHFFFAOYSA-N 0.000 description 2
- 239000010953 base metal Substances 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 241000609240 Ambelania acida Species 0.000 description 1
- 229910001020 Au alloy Inorganic materials 0.000 description 1
- ODINCKMPIJJUCX-UHFFFAOYSA-N Calcium oxide Chemical compound [Ca]=O ODINCKMPIJJUCX-UHFFFAOYSA-N 0.000 description 1
- 229910001208 Crucible steel Inorganic materials 0.000 description 1
- 229910000861 Mg alloy Inorganic materials 0.000 description 1
- 229910019094 Mg-S Inorganic materials 0.000 description 1
- 229910019397 Mg—S Inorganic materials 0.000 description 1
- 229910000676 Si alloy Inorganic materials 0.000 description 1
- 229910008455 Si—Ca Inorganic materials 0.000 description 1
- 230000005856 abnormality Effects 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 239000010905 bagasse Substances 0.000 description 1
- 239000000292 calcium oxide Substances 0.000 description 1
- 235000012255 calcium oxide Nutrition 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 230000006866 deterioration Effects 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
- 238000002474 experimental method Methods 0.000 description 1
- 238000009413 insulation Methods 0.000 description 1
- 239000000395 magnesium oxide Substances 0.000 description 1
- 230000013011 mating Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052863 mullite Inorganic materials 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 239000002904 solvent Substances 0.000 description 1
- 230000008646 thermal stress Effects 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
Landscapes
- Coating By Spraying Or Casting (AREA)
Abstract
Description
【発明の詳細な説明】 （発明の対象） 本発明は溶射皮膜を形成する方法に関するものである。[Detailed description of the invention] (Subject of invention) The present invention relates to a method of forming a thermal spray coating.
（従来技術）
内燃機関用部材は長期にわたり高温状態で連続運転に耐
え、しかも熱サイクルを受けるため耐熱耐食性と共に機
械的強度を要求され、とくに内燃機関のピストンおよび
ピストンヘッド材等はそれが溶剤材である場合には溶射
皮膜の耐剥離性に対して高度な要求がある。(Prior art) Internal combustion engine parts are required to withstand continuous operation at high temperatures for long periods of time and to be subjected to thermal cycles, so they are required to have mechanical strength as well as heat resistance and corrosion resistance.In particular, internal combustion engine piston and piston head materials are made of solvent-resistant materials. In this case, there are high demands on the peeling resistance of the thermal spray coating.
たとえばガスタービンにおいてはＮｉ基合金基材上にま
づＮｉ−Ｃｒ合金を溶射し更にその上にＺｒＯ２系セラ
ミックを溶射したものがあるが斯様な皮膜はタービン使
用中に溶射皮膜の剥離を生じやすい欠点がある。For example, in some gas turbines, a Ni-Cr alloy is first sprayed on a Ni-based alloy base material, and then a ZrO2-based ceramic is sprayed on top of that, but such coatings tend to peel off during use of the turbine. There are some easy drawbacks.
また、鋳鋼製ピストン材の表面にＮｉ−Ｃｒ合金を溶射
し更にその上にＺｒＯ２を溶射したものを実用試験した
結果はやはり溶射皮膜の剥離が生起し易く、したがって
剥離を防ぐにはＺｒＯ２の溶射厚さを薄くシなければ使
用出来ないがこれによって耐熱性および耐摩耗性を犠牲
にしなければならない。In addition, the results of a practical test of a Ni-Cr alloy sprayed onto the surface of a cast steel piston material and then ZrO2 sprayed on top showed that the sprayed coating was likely to peel off, and therefore, ZrO2 spraying was necessary to prevent peeling. It cannot be used unless the thickness is reduced, but this requires sacrificing heat resistance and abrasion resistance.
さらに、 １合金製ピストンに対し、その表面にＮｉ−
Ｃｒ合金またはＮｉ −１ｊ材を下地溶射したのちＺｒ
’Ｏｑを溶射して断熱する方法を試みた結果□は実用エ
ンジン試験によって比較的短時間内に溶射層の剥離を生
じ使用に堪えなくなることが知られている。Furthermore, Ni-
After spraying Cr alloy or Ni-1j material on the base, Zr
As a result of trying the thermal insulation method by spraying Oq, it is known that the sprayed layer peels off within a relatively short period of time in a practical engine test, making it unusable.
斯様な剥離原因は基材と溶射仕上げ層の酸化物層との熱
膨張係数の差異が犬なるためである。すなわち−ト記各
材の熱膨張係数を測定すれば第１表のような結果が得ら
れ、各材質の熱膨張係数の差異は顕著である。The cause of such peeling is the difference in thermal expansion coefficient between the base material and the oxide layer of the sprayed finish layer. That is, if the coefficient of thermal expansion of each material is measured, the results shown in Table 1 are obtained, and the difference in the coefficient of thermal expansion of each material is remarkable.
（第１表）
表から明らかな通りＡ１合金基材上にＮｉ−Ｃｒ合金を
溶射し更にＺｒＯ２溶射したものは各層間において、は
ぼ（２〜８） Ｘ １０’／ ’Ｏの熱１膨張率差があ
り皮膜剥離の原因をなすことは明白である。斯様な剥離
部分をしらべると、しばしばノ、（材と下地層との境域
面において剥離を認めることができるのである。(Table 1) As is clear from the table, when the Ni-Cr alloy was sprayed on the A1 alloy base material and then ZrO2 was sprayed, the thermal expansion of (2 to 8) x 10'/'O was between each layer. It is clear that there is a difference in rate and this is the cause of film peeling. When examining such peeled areas, it is often possible to see peeling at the interface between the material and the underlying layer.
（発明の目的）
本発明の目的は上記従来技術の欠点を改良し耐剥離性に
すぐれたセラミック＃射皮膜の形成方法を提供すること
にある。(Object of the Invention) An object of the present invention is to provide a method for forming a ceramic spray coating having excellent peeling resistance and improving the above-mentioned drawbacks of the prior art.
（発明の構成）
本発明は２５０〜４００”０に加熱したｌまたはＡ４合
金基材にまずＣｒ ’１５〜２５重星％を含む旧−Ｃｒ
合金またはＡｆＬ４〜２２重量％を含む旧−Ａ１合金あ
るいは前記Ｎｉ−Ｃｒ合金にＡｎ ４〜２２重量％を添
加したＮｉ−Ｃｒ−Ａｌ１合金を溶射して下地層を形成
し、次いでこの下地層の表面に安定化ＺｒＯ２系セラミ
ック材を溶射することを特徴とする溶射皮膜形成方法に
ある。(Structure of the Invention) The present invention is based on a former -Cr alloy containing 15 to 25% of Cr' to a l or A4 alloy base material heated to 250 to 400"0.
An underlayer is formed by thermal spraying an old-A1 alloy containing 4-22% by weight of AfL or a Ni-Cr-Al1 alloy in which 4-22% by weight of An is added to the Ni-Cr alloy, and then the underlayer is A method for forming a thermal spray coating is characterized in that a stabilized ZrO2-based ceramic material is thermally sprayed onto a surface.
本発明に謂うＡＭまたはＡ１合金とは純Ａ文または人文
−１１１ｇ系、 Ａ文−Ｓｉ系、Ａ９．− Ｍｇ −Ｓ
ｉ系、ＡＬＬ−Ｓｉ−Ｃａ系、ｌｊ −５ｉ−Ｆｅ系を
含むものである。The AM or A1 alloy referred to in the present invention is pure A-type or human-111g type, A-type-Si type, A9. -Mg-S
These include i-based, ALL-Si-Ca-based, and lj-5i-Fe-based.
また下地材として使用されるＮｉ −Ｃｒ合金、Ｎｉ
−ヘ立合金またはＮ１−Ｃｒ−Ａ文合金はそれぞれの粒
度 １０５〜：ｌ’、Ｏｇｍの範囲の比較的粗粒の粉末
であり斯様な粉末の使用によりセラミック溶射皮膜との
接合強度向上のために好ましい。Ｎｉ −Ｃｒ合金にお
いてはＯｒ品位が１５〜２５重量％、Ｎｉ −Ａ１合金
においてはＡ文品位が４〜２２重量％、Ｎ１−Ｃｒ−Ａ
文合金においては１品位が４〜２２重量％、クロム品位
が１５〜２５重量％であることを要する。しかし実験結
果によればＡＭ−２０％Ｓｉ合金等も下地材として溶射
皮膜の接合力向−Ｌ効果は大であることが確認されてい
る。In addition, Ni-Cr alloy used as a base material, Ni
- Hetachi alloy or N1-Cr-A alloy is a relatively coarse powder with a particle size in the range of 105 to 1', Ogm, and the use of such powder improves the bonding strength with the ceramic spray coating. preferred for. In the Ni-Cr alloy, the Or grade is 15 to 25% by weight, in the Ni-A1 alloy, the A grade is 4 to 22% by weight, and the N1-Cr-A
In the alloy, the 1 grade is required to be 4 to 22% by weight, and the chromium grade is required to be 15 to 25% by weight. However, according to experimental results, it has been confirmed that AM-20%Si alloy and the like have a large bonding force -L effect when used as a base material for a thermally sprayed coating.
なおここにいうＮｉ−Ａ１合金、Ｎ１−Ｇｒ−Ａｌ１合
金とは、Ｎｉ又はＮｉ−Ｃｒ合金に被覆された複合粉末
あるいは旧、Ｃｒ、 Ａｎの微粉造粒粉末、又は各成分
の金属結合合金粉末のいずれであっても良い。Note that the Ni-A1 alloy and N1-Gr-Al1 alloy referred to herein refer to composite powder coated with Ni or Ni-Cr alloy, fine granulated powder of old, Cr, and An, or metal-bonded alloy powder of each component. It may be either.
本発明の特徴の一つは前記した通りＡＱまたはＡ文合金
基材を温度２５０〜４００’Ｏに加熱した状態において
上記下地材を溶射する点にある。水弁明治は多数の実験
の結果、基材加熱温度２５０℃以下においては加熱の効
果は比較的弱く、また４００℃を超えるときは基材の軟
化変形を生じ易いのみならず溶射皮膜の接合力向上効果
も飽和に達するため４００℃以上の加熱は本発明達成の
ため好ましくないことが確認された。なお基材の加熱に
際しては、特に３５０℃以上の高温加熱の場合は、基材
の変質をさける為、短時間の加熱で所定温度とし、すみ
やかに下地溶射することが望ましい。下地溶射の厚さは
、０．０５〜０，２１の範囲が適しており、０．０５ｍ
ｍ以下では熱応力緩和の効果が弱く、一方０．２ｍｍを
超えると溶射加工費がかさむのみで効果の向−トは期待
できない。One of the features of the present invention is that, as described above, the base material is thermally sprayed on the AQ or A pattern alloy base material while it is heated to a temperature of 250 to 400'O. As a result of numerous experiments, Mizuben Meiji has found that the heating effect is relatively weak when the base material heating temperature is below 250℃, and when it exceeds 400℃, it is easy to cause softening and deformation of the base material, as well as the bonding strength of the thermal spray coating. It was confirmed that heating at 400° C. or higher is not preferable for achieving the present invention because the improving effect also reaches saturation. When heating the base material, especially when heating at a high temperature of 350° C. or higher, it is desirable to heat the base material for a short time to reach a predetermined temperature and immediately spray the base material in order to avoid deterioration of the base material. The thickness of the base thermal spray is suitable in the range of 0.05 to 0.21, and 0.05 m
If the thickness is less than 0.2 mm, the thermal stress relaxation effect will be weak, while if it exceeds 0.2 mm, the cost of thermal spraying will increase and no further effect can be expected.
また本発明にいうセラミック溶射材は高温安定性良好で
、しかも熱伝導率が低く、更に熱膨張係数は可能な限り
基材金属ならびに下地材金属の熱膨張係数に近いものが
良い。斯様な性質を有するセラミック材としてはアルミ
ナ、ムライト、安定化ジルコニア、カルシア、イツトリ
ア、マグネシア等があげられるが、特に安定化ジルコニ
アが好適である。Further, the ceramic sprayed material according to the present invention has good high temperature stability and low thermal conductivity, and preferably has a coefficient of thermal expansion as close to that of the base metal and base metal as possible. Ceramic materials having such properties include alumina, mullite, stabilized zirconia, calcia, ittria, magnesia, etc., and stabilized zirconia is particularly preferred.
セラミック材の溶射厚さは０．２〜１．０ ｍｍの範囲
が最適である。０．２川ｍ以ドの７ましい皮膜は断熱効
果に乏しい欠点があり、また１、０ｍｍ以上の厚い皮膜
は耐剥離性低下はまぬがれない。The optimum spray thickness of the ceramic material is in the range of 0.2 to 1.0 mm. A film with a thickness of 0.2 mm or more has the disadvantage of poor heat insulating effect, and a film with a thickness of 1.0 mm or more inevitably suffers from a decrease in peeling resistance.
本発明の方法により加熱された基材に下地材を溶射後、
醇化物セラミック材を溶射することによって得られる溶
剤加−に体は熱サイクル環境下において長期間使用して
も溶射皮膜の剥剛、亀裂等を生起しないものとなる。そ
の理由は加熱基材と下地溶射層の密着性は基材を加熱し
ない場合に比較して膨張状態の基材に下地層が喰い込む
ごと〈溶用ｙれるため密着性をいちじるしく向上するの
に加え、この下地層に熱膨張係数の低いジルコニアが溶
射されるため結局、基材、下地材およびシルコニ７層の
熱膨張係数の差異を実質的に接近せしめる効果が発揮さ
れるためと占えられる。After spraying the base material onto the heated base material by the method of the present invention,
The solvent-added body obtained by thermal spraying a fused ceramic material does not cause peeling, cracking, etc. of the thermal sprayed coating even when used for a long period of time in a thermal cycle environment. The reason for this is that the adhesion between the heated base material and the base sprayed layer is significantly improved as the base layer bites into the expanded base material compared to when the base material is not heated. In addition, since zirconia having a low coefficient of thermal expansion is thermally sprayed onto this base layer, it is believed that the effect of substantially reducing the difference in coefficient of thermal expansion between the base material, the base material, and the seven layers of silcony is achieved.
本発明において安定化ジルコニアを使用する理由は次の
通りである。The reason for using stabilized zirconia in the present invention is as follows.
安定化ジルコニアとは、加熱・冷却において特定温度で
変態しその際急激な体積変化を起す純ジルコニアに対し
Ｙ２Ｏ３、ＣａＯｌＭｇＯ等が数％以−１−添加され、
常温から高温まで変態による急激な体積変化を起さない
構造をしたジルコニアである。又ジルコニアの熱膨張係
数が金属に近く高いことから熱サイクルを受ける部材の
コーティングに対しクラック等が生じにくく最適である
。Stabilized zirconia is pure zirconia that transforms at a specific temperature during heating and cooling and undergoes a rapid volume change.
Zirconia has a structure that does not cause rapid volume changes due to transformation from room temperature to high temperature. Also, since zirconia has a high coefficient of thermal expansion close to that of metal, it is ideal for coating parts that undergo thermal cycles because it is less likely to cause cracks.
（実施例１）
純ＡｆＬ、 Ａ文−１３％８１合金およびＡ文−１，
５％Ｍｇ合金基材にＮｉ−Ｃｒ合金、Ｎｉ−Ａｕ合金ま
たはＮ１−Ｃｒ−Ａ文合金を２５０〜４００℃に加熱さ
れた基材上に溶射し、次いで各種酸化物粉末を仕−■−
げ溶射した試片について熱サイクル処理後、溶射皮膜の
中張り試験を行い皮膜の１Ｔｉ４！ｌｌ離性をしらべた
。溶射条件、熱サイクル試験条件および引張り試験条件
は次に示す通りであり、試験結果を第２表に示す。(Example 1) Pure AfL, A-13% 81 alloy and A-1,
Ni-Cr alloy, Ni-Au alloy, or N1-Cr-A alloy is thermally sprayed onto a 5% Mg alloy base material heated to 250 to 400°C, and then various oxide powders are applied.
After thermal cycle treatment of the thermally sprayed specimens, a lining test of the thermally sprayed coating was conducted to determine the coating's 1Ti4! I investigated the releasability. The thermal spraying conditions, thermal cycle test conditions and tensile test conditions are as shown below, and the test results are shown in Table 2.
下地層溶射条件：アークガスとしてＡｒガス使用量３１
ｊ／ｍｉｎ補助ガスとしてＨｅガス使用量７、Ｑ／ｍｉ
ｎ溶射距離１１０ｍｍ、溶射皮膜厚さ０．１ｍｍ （プ
ラズマダイン社ＳＧ−１００プラズマ溶射ガン使用）
仕１−げ層溶射条件：Ａ丁カス３８．ｕ ／ ｍｉｎ
、 Ｈｅバガス５立／ｍｉｎ、溶射距離９０ｍｍ、溶射
皮膜厚さ０．４ｍｍ （プラズマダイン社５Ｇ−１００
プラズマ溶射ガン使用）
熱サイクル試験条件：溶射後の試片を４００ ’Ｏの炉
内に２０分間保持後空冷する過程を１０回繰り返す。Base layer thermal spraying conditions: Ar gas usage amount as arc gas: 31
j/min He gas usage as auxiliary gas 7, Q/min
Spraying distance: 110 mm, spray coating thickness: 0.1 mm (using Plasma Dyne's SG-100 plasma spray gun) Finishing layer spraying conditions: A-cut 38. u/min
, He bagasse 5 m/min, spray distance 90 mm, spray coating thickness 0.4 mm (Plasma Dyne 5G-100
(using a plasma spray gun) Thermal cycle test conditions: The process of holding the sprayed specimen in a 400'O furnace for 20 minutes and then cooling it in air is repeated 10 times.
引張り試験条件：熱サイクル試験後の試片の端面溶射皮
膜部と相手材純アルミニウムを接着剤アラルダイ１−Ａ
Ｔ−１にて接着後引張り試験に供す。Tensile test conditions: After the thermal cycle test, the thermal sprayed coating on the end face of the specimen and the mating material pure aluminum were glued together using Araldye 1-A.
After adhesion, it is subjected to a tensile test at T-1.
試験結果：各試験とも５試料の実測値または平均値。Test results: Each test is the actual value or average value of 5 samples.
（以下余白）
（比較例）
実施例１と同一基材と各種下地材および各種酸化物を用
い、基材を加熱せず、または２５０℃以下もしくは４０
０℃以上の加熱状態において実施例１と同様の方法によ
り溶射および試験を行なった結果、第３表に示す結果を
得た。(Margin below) (Comparative example) Using the same base material as in Example 1, various base materials, and various oxides, without heating the base material, or at 250 ° C. or lower or 40 ° C.
Thermal spraying and testing were conducted in the same manner as in Example 1 under heating conditions of 0° C. or higher, and the results shown in Table 3 were obtained.
（以下余白）
以上、実施例１および比較例を見るに、加熱せず、また
は本発明の加熱温度範囲を逸脱する温度に加熱した基材
に下地溶射を施したものは引張り強度が低いのみならず
強度のばらつきが大であるのに対し本発明方法によれば
引張強度は高く、引張り特性にばらつきが少く、母材−
下地間での剥離も見られず、仕」二層内で安定して破断
していることから判断して本発明方法により耐剥離性の
改善は顕著であることが知られる。(Left below) Looking at Example 1 and Comparative Examples, it can be seen that the tensile strength of the base material that is not heated or that is heated to a temperature outside the heating temperature range of the present invention and that is subjected to base thermal spraying is low. However, according to the method of the present invention, the tensile strength is high, there is little variation in tensile properties, and the base material
Judging from the fact that no peeling was observed between the bases and stable fracture occurred within the two layers, it is known that the method of the present invention significantly improves the peeling resistance.
（実施例２）
径５０ｍｍφのローエックスＡ１合金製ピストンの頂部
に実施例１．Ｎｏ、４および比較例陥、２と同様の溶射
を行なった後１２５ｃｃ、５０００サイクル／分のガソ
リンエンジン実機において１０時間運転１時間停止の間
けつ運転でエンジンテストを実施した結果、前者は２０
サイクルの運転テスト後においても溶射皮膜に剥離、亀
裂等の異常は全く観察されなかった。しかるに後者は２
サイクル目の運転後エンジン内を調べたところ、ピスト
ン頂部溶射皮膜の約３０％に欠落が観察された。(Example 2) Example 1 was applied to the top of a Roex A1 alloy piston with a diameter of 50 mmφ. After thermal spraying in the same manner as in No. 4 and Comparative Example No. 2, an engine test was conducted using an actual gasoline engine of 125 cc and 5,000 cycles/min by running it for 10 hours and stopping for 1 hour, and found that the former was 20
Even after the cycle operation test, no abnormalities such as peeling or cracking were observed in the sprayed coating. However, the latter is 2
When the inside of the engine was examined after the cycle of operation, it was observed that about 30% of the sprayed coating on the top of the piston was missing.
以上の結果から本発明方法によって形成された溶射皮膜
の耐剥離性は極めて良好であることは明らかである。From the above results, it is clear that the peeling resistance of the thermal sprayed coating formed by the method of the present invention is extremely good.
Claims (1)
ムまたはアルミニウム合金基材に、下地層としてアルミ
ニウム４〜２２重量％を含有するニッケル−アルミニウ
ム合金、またはクロム１５〜２５重量％を含有するニッ
ケル−クロム合金、あるいはクロム１５〜２５重量％と
アルミニウム４〜２２重量％を含有するニッケル−クロ
ム−アルミニウム合金のうちいずれが１種を溶射し、次
いで該下地層の上にセラミック材料を溶射することを特
徴とするセラミック溶射皮膜形成方法。 ２）セラミック材料が安定化ジルコニア系材料であるこ
とを特徴とする特許請求の範囲第１項の方法。[Claims] 1) A nickel-aluminum alloy containing 4 to 22% by weight of aluminum or 15 to 25% by weight of chromium is applied as a base layer to an aluminum or aluminum alloy base material heated to 250°C to 400°C. A nickel-chromium alloy containing 15 to 25% by weight of chromium and a nickel-chromium-aluminum alloy containing 4 to 22% by weight of aluminum is thermally sprayed, and then a ceramic material is applied onto the base layer. A method for forming a ceramic thermal spray coating characterized by thermal spraying. 2) A method according to claim 1, characterized in that the ceramic material is a stabilized zirconia-based material.
Priority Applications (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60047400A JPS61207566A (en) | 1985-03-12 | 1985-03-12 | Formation of thermally sprayed ceramic film |
| US07/408,951 US5204189A (en) | 1985-03-12 | 1989-09-18 | Heat-sensitive transferring recording medium |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60047400A JPS61207566A (en) | 1985-03-12 | 1985-03-12 | Formation of thermally sprayed ceramic film |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS61207566A true JPS61207566A (en) | 1986-09-13 |
| JPH0515781B2 JPH0515781B2 (en) | 1993-03-02 |
Family
ID=12774059
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP60047400A Granted JPS61207566A (en) | 1985-03-12 | 1985-03-12 | Formation of thermally sprayed ceramic film |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS61207566A (en) |
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63274751A (en) * | 1987-05-01 | 1988-11-11 | Toyota Motor Corp | Ceramic thermally sprayed member |
| US4885213A (en) * | 1986-11-05 | 1989-12-05 | Toyota Jidosha Kabushiki Kaisha | Ceramic-sprayed member and process for making the same |
| US5204302A (en) * | 1991-09-05 | 1993-04-20 | Technalum Research, Inc. | Catalyst composition and a method for its preparation |
| EP0707091A1 (en) * | 1994-09-16 | 1996-04-17 | Praxair S.T. Technology, Inc. | Zirconia-based tipped blades having macrocracked structure and process for producing it |
| FR2763259A1 (en) * | 1997-05-16 | 1998-11-20 | Ecia Equip Composants Ind Auto | Catalyst-reinforced composite material for use in an automobile catalytic converter |
| JP2006097042A (en) * | 2004-09-28 | 2006-04-13 | Hitachi Ltd | Heat resistant member having thermal barrier coating and gas turbine |
| JP2007083692A (en) * | 2005-09-26 | 2007-04-05 | Tohoku Univ | Metal-glass composite material and member for electronic-electric instrument using it |
| US7364798B2 (en) | 1999-12-10 | 2008-04-29 | Tocalo Co., Ltd. | Internal member for plasma-treating vessel and method of producing the same |
| US8877002B2 (en) | 2002-11-28 | 2014-11-04 | Tokyo Electron Limited | Internal member of a plasma processing vessel |
| WO2015190325A1 (en) * | 2014-06-11 | 2015-12-17 | 日本発條株式会社 | Method for producing laminate, and laminate |
| JP2017226923A (en) * | 2017-09-20 | 2017-12-28 | 日本発條株式会社 | Laminate and production method of laminate |
-
1985
- 1985-03-12 JP JP60047400A patent/JPS61207566A/en active Granted
Cited By (16)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4885213A (en) * | 1986-11-05 | 1989-12-05 | Toyota Jidosha Kabushiki Kaisha | Ceramic-sprayed member and process for making the same |
| JPS63274751A (en) * | 1987-05-01 | 1988-11-11 | Toyota Motor Corp | Ceramic thermally sprayed member |
| JPH0527706B2 (en) * | 1987-05-01 | 1993-04-22 | Toyota Motor Co Ltd | |
| US5204302A (en) * | 1991-09-05 | 1993-04-20 | Technalum Research, Inc. | Catalyst composition and a method for its preparation |
| EP0707091A1 (en) * | 1994-09-16 | 1996-04-17 | Praxair S.T. Technology, Inc. | Zirconia-based tipped blades having macrocracked structure and process for producing it |
| FR2763259A1 (en) * | 1997-05-16 | 1998-11-20 | Ecia Equip Composants Ind Auto | Catalyst-reinforced composite material for use in an automobile catalytic converter |
| US7364798B2 (en) | 1999-12-10 | 2008-04-29 | Tocalo Co., Ltd. | Internal member for plasma-treating vessel and method of producing the same |
| US8877002B2 (en) | 2002-11-28 | 2014-11-04 | Tokyo Electron Limited | Internal member of a plasma processing vessel |
| JP2006097042A (en) * | 2004-09-28 | 2006-04-13 | Hitachi Ltd | Heat resistant member having thermal barrier coating and gas turbine |
| JP4607530B2 (en) * | 2004-09-28 | 2011-01-05 | 株式会社日立製作所 | Heat resistant member having a thermal barrier coating and gas turbine |
| US7901790B2 (en) | 2004-09-28 | 2011-03-08 | Hitachi, Ltd. | High temperature component with thermal barrier coating and gas turbine using the same |
| JP2007083692A (en) * | 2005-09-26 | 2007-04-05 | Tohoku Univ | Metal-glass composite material and member for electronic-electric instrument using it |
| WO2015190325A1 (en) * | 2014-06-11 | 2015-12-17 | 日本発條株式会社 | Method for producing laminate, and laminate |
| JP2016000849A (en) * | 2014-06-11 | 2016-01-07 | 日本発條株式会社 | Production method of laminate, and laminate |
| US10315388B2 (en) | 2014-06-11 | 2019-06-11 | Nhk Spring Co., Ltd. | Method of manufacturing laminate and laminate |
| JP2017226923A (en) * | 2017-09-20 | 2017-12-28 | 日本発條株式会社 | Laminate and production method of laminate |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0515781B2 (en) | 1993-03-02 |
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