JPH0633221A - Ti cementation method of ti-al based alloy member - Google Patents
Ti cementation method of ti-al based alloy memberInfo
- Publication number
- JPH0633221A JPH0633221A JP18706092A JP18706092A JPH0633221A JP H0633221 A JPH0633221 A JP H0633221A JP 18706092 A JP18706092 A JP 18706092A JP 18706092 A JP18706092 A JP 18706092A JP H0633221 A JPH0633221 A JP H0633221A
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- treatment
- diffusion
- alloy member
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- Other Surface Treatments For Metallic Materials (AREA)
Abstract
Description
【0001】[0001]
【産業上の利用分野】本発明はTi−Al系合金部材へ
のTi拡散浸透処理方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method of Ti diffusion and infiltration treatment for a Ti-Al alloy member.
【0002】[0002]
【従来の技術】Ti−Al二元系において、常温におけ
る35〜42原子%Alの組成域において、金属間化合
物TiAlが存在し、この金属間化合物は比重が約3.
8と軽量で、かつ、1070Kまでの耐力が400MP
a以上等の優れた力学的特性を持つため、軽量耐熱構造
材として、エンジンやタービン等への実用化が期待され
ている。2. Description of the Related Art In a Ti-Al binary system, an intermetallic compound TiAl is present in a composition range of 35 to 42 atomic% Al at room temperature, and the intermetallic compound has a specific gravity of about 3.
Light weight of 8 and yield strength of 400MP up to 1070K
Since it has excellent mechanical properties such as a or higher, it is expected to be put to practical use in engines, turbines, etc. as a lightweight heat resistant structural material.
【0003】しかしながら、金属間化合物TiAlは軽
量で高温強度、クリープ強度には優れているが、硬度が
低いため表面の耐摩耗性が劣り、高い耐摩耗性を要求さ
れる摺動部材へ適用するためには、表面硬化処理をする
必要があった。However, although the intermetallic compound TiAl is light in weight and excellent in high temperature strength and creep strength, it has poor hardness due to its low hardness and is applied to sliding members which are required to have high wear resistance. In order to do so, it was necessary to carry out a surface hardening treatment.
【0004】例えば、特開平2−47278号公報の耐
摩耗性Ti系部材の発明においては、実質的にTiAl
からなる基材の耐摩耗性が要求される部位の表面層に、
アルミニウム粉末を配し、レーザ光を照射することによ
り、Al濃度が48%以上のTiAl3層を主体とする
層を形成し、耐摩耗性を向上しており、また、特開平3
−229884号公報の耐摩耗性チタン合金部材の発明
においては、TiAlからなる基材の耐摩耗性が要求さ
れる部位に、ブラズマ肉盛法を用いてアルミニウム28
〜31%を含む主としてTi3Alからなる耐摩耗層を
形成し、耐摩耗性の優れた部材を得ている。For example, in the invention of a wear-resistant Ti-based member disclosed in Japanese Patent Laid-Open No. 2-47278, TiAl is substantially used.
In the surface layer of the part where the wear resistance of the base material consisting of is required,
By disposing an aluminum powder and irradiating it with laser light, a layer mainly composed of a TiAl 3 layer having an Al concentration of 48% or more is formed, and wear resistance is improved.
In the invention of the wear-resistant titanium alloy member of JP-A-229884, the aluminum 28 is formed by using the plasma overlay method on the site where the wear resistance of the base material made of TiAl is required.
A wear resistant layer mainly made of Ti 3 Al containing up to 31% is formed to obtain a member having excellent wear resistance.
【0005】特開平3−75385号公報のTiAl基
合金製摺動部用部品の発明においては、これらTiAl
系合金をエンジンバルブとして用いるには充分な耐摩耗
性を具備しないことを指摘すると共に、TiAl合金部
材の表面を、物理的プロセスによる気相メッキまたはガ
ス窒化等の処理によって、厚さ2〜10μmの窒化チタ
ン層で被覆することにより、耐摩耗性が改善されること
が開示されている。In the invention of the sliding part made of a TiAl-based alloy disclosed in JP-A-3-75385, these TiAl
It is pointed out that the TiAl alloy member does not have sufficient wear resistance to be used as an engine valve, and the surface of the TiAl alloy member is subjected to a physical process such as vapor phase plating or gas nitriding to have a thickness of 2 to 10 μm. It is disclosed that the wear resistance is improved by coating with the titanium nitride layer.
【0006】[0006]
【発明が解決しようとする課題】ところで、前記特開平
2−47278号公報の耐摩耗性Ti系部材の発明にお
いては、表面層にアルミニウム粉末を配し、レーザ光を
照射することにより、耐摩耗層を形成しており、また前
記特開平3−229884号公報の耐摩耗性チタン合金
部材の発明においては、ブラズマ肉盛法を用いて耐摩耗
層を形成している。By the way, in the invention of the wear-resistant Ti-based member disclosed in Japanese Patent Laid-Open No. 2-47278, wear resistance is improved by arranging aluminum powder on the surface layer and irradiating with laser light. In addition, in the invention of the wear-resistant titanium alloy member disclosed in JP-A-3-229884, the wear-resistant layer is formed by using the plasma overlay method.
【0007】しかしながら、この様な方法は、例えば自
動車用エンジンバルブフェースのような限られた部位
(小面積部位)には適しているが、複雑な形状の部品表
面全体であるとか、大面積部位への適用は困難である。However, although such a method is suitable for a limited portion (small area portion) such as an engine valve face for an automobile, for example, the entire surface of a part having a complicated shape, or a large area portion. Is difficult to apply.
【0008】本発明はTi−Al合金部材の表面硬化処
理の前記のごとき問題点を解決すべく発明されたもので
あって、Ti−Al合金部材の耐摩耗性を必要とする摺
動部材への適用において、大面積部位あるいは複雑形状
部位への表面硬化処理が可能な処理方法を提供すること
を目的とする。The present invention has been invented to solve the above-mentioned problems in surface hardening treatment of a Ti-Al alloy member, and to a sliding member which requires wear resistance of the Ti-Al alloy member. It is an object of the present invention to provide a treatment method capable of performing a surface hardening treatment on a large-area portion or a complex-shaped portion in the application.
【0009】[0009]
【課題を解決するための手段】発明者は、Ti−Al金
属間化合物を主体とする基材の耐摩耗性を必要とする部
位に、アルミニウム28〜31%を含む主としてTi3
Alからなる耐摩耗層を形成すると、摺動部材としの耐
摩耗性が確保できることに鑑み、Tiを拡散浸透させる
ことを着想し、Ti−Al合金部材のTi拡散方法につ
いて鋭意研究を重ねた。その結果、基材の表面に適量の
Ti粉末とハロゲン化物およびセラミック粉末の混合粉
末を接触させて加熱することにより、Tiを拡散浸透で
きることを見出して本発明を完成した。DISCLOSURE OF THE INVENTION The inventor of the present invention has mainly used Ti 3 containing 28 to 31% of aluminum in a portion requiring wear resistance of a base material mainly composed of a Ti—Al intermetallic compound.
Considering that the wear resistance of the sliding member can be ensured by forming the wear resistant layer made of Al, the idea of diffusing and permeating Ti was conceived, and earnest studies were conducted on the Ti diffusion method of the Ti—Al alloy member. As a result, they have found that Ti can be diffused and permeated by bringing an appropriate amount of Ti powder and a mixed powder of a halide and a ceramic powder into contact with the surface of the base material and heating the mixture to complete the present invention.
【0010】本発明のTi−Al系合金部材へのTi拡
散浸透処理方法は、Ti−Al系合金からなる基材を、
混合比で10〜60wt%のチタン粉末と、10wt%
以下のハロゲン化合物と、残部がセラミック粉末からな
る処理粉末で覆い、不活性雰囲気中で加熱して、Tiを
拡散させることを要旨とする。また、本発明では、必要
に応じて、さらにTiを拡散させたTi−Al系合金か
らなる基材を、前記処理粉末から取り出し、さらに不活
性雰囲気中で、700〜1100℃で10〜50時間の
加熱処理を行う。The Ti diffusion and infiltration treatment method for a Ti-Al alloy member of the present invention comprises:
Mixing ratio of 10 to 60 wt% titanium powder and 10 wt%
The gist of the present invention is to cover the following halogen compound and the treated powder of which the remainder is ceramic powder, and heat in an inert atmosphere to diffuse Ti. Further, in the present invention, if necessary, a base material made of a Ti—Al-based alloy in which Ti is further diffused is taken out from the treated powder, and further in an inert atmosphere at 700 to 1100 ° C. for 10 to 50 hours. Heat treatment.
【0011】本発明のTi−Al系合金は、Al33〜
38重量%を含むTi−Al合金からなる。Al33〜
38重量%はTiAlを主とするTi−Al系金属間化
合物の組成範囲である。ここに、TiAlを主とするT
i−Al系金属間化合物とは、TiAl金属間化合物を
主として含み、他にTiAl2、TiAl3、Ti3Al
等の金属間化合物を含むものをいう。The Ti--Al based alloy of the present invention comprises Al33-
It consists of a Ti-Al alloy containing 38% by weight. Al33 ~
38% by weight is the composition range of the Ti-Al based intermetallic compound mainly composed of TiAl. Here, T mainly composed of TiAl
The i-Al-based intermetallic compound mainly includes a TiAl intermetallic compound, and also includes TiAl 2 , TiAl 3 , and Ti 3 Al.
And the like include intermetallic compounds.
【0012】Alが33重量%未満ではTiAl合金中
のTiAl金属間化合物の割合が少なくなって低比重、
高温強度およびクリープ強度の向上が充分でなく、、A
lが38重量%を越えるとTiAl3金属間化合物が晶
出しやすくなって脆くなる。このため、基材のAlが3
3〜38重量%を外れると、耐摩耗性チタン合金部材の
強度特性が劣る。If the Al content is less than 33% by weight, the proportion of the TiAl intermetallic compound in the TiAl alloy is small, resulting in a low specific gravity.
The improvement in high temperature strength and creep strength is not sufficient,
If 1 exceeds 38% by weight, the TiAl 3 intermetallic compound tends to crystallize and becomes brittle. Therefore, the Al content of the base material is 3
If it is out of the range of 3 to 38% by weight, the strength characteristics of the wear resistant titanium alloy member will be poor.
【0013】処理粉末は、拡散浸透しようとする金属粉
末、金属粉末の焼結防止用のアルミナ、カオリン等のセ
ラミック粉末、金属粉末に活性化吸着し解離する塩化ア
ンモニウムまたはハロゲン化物からなる。拡散浸透処理
は被処理部材のまわりに処理粉末を充填するいわゆる粉
末充填法により行われる。処理温度は700〜1100
℃の温度域とし、処理時間は2〜20時間とすることが
好ましい。The treated powder is composed of a metal powder that tends to diffuse and permeate, an alumina for preventing sintering of the metal powder, a ceramic powder such as kaolin, and ammonium chloride or a halide that is activated and adsorbed to and dissociates from the metal powder. The diffusion permeation treatment is performed by a so-called powder filling method in which the treated powder is filled around the member to be treated. Processing temperature is 700-1100
It is preferable that the temperature is in the temperature range of ° C and the treatment time is 2 to 20 hours.
【0014】上記処理で膜厚が不十分な時は、上記処理
後に被処理物を粉末中より取り出し、熱処理によって拡
散深さ(改質厚さ)を拡大することも可能である。その
際の条件としては、不活性雰囲気にて700〜1100
の温度範囲で10〜50時間行う。When the film thickness is insufficient by the above treatment, it is possible to take out the object to be treated from the powder after the above treatment and increase the diffusion depth (modified thickness) by heat treatment. The conditions at that time are 700 to 1100 in an inert atmosphere.
The temperature range is 10 to 50 hours.
【0015】[0015]
【作用】Ti−Al系合金部材は処理粉末中で熱処理し
てTiを拡散浸透させるので、処理面積の大きな部材で
も、また複雑形状の部材であっても、処理が可能であ
り、耐摩耗性に優れたTi−Al系合金部材が得られ
る。さらに、必要に応じて700〜1100℃で10〜
50時間の加熱処理を行うことにより、Tiがより深部
まで拡散浸透して、耐摩耗性のある拡散深さが拡大され
る。The Ti-Al alloy member is heat-treated in the treated powder to diffuse and infiltrate Ti. Therefore, even a member having a large treated area or a member having a complicated shape can be treated and wear resistance is improved. An excellent Ti-Al alloy member can be obtained. Further, if necessary, 10 at 700 to 1100 ° C.
By performing the heat treatment for 50 hours, Ti diffuses and penetrates to a deeper portion, and the diffusion depth having abrasion resistance is expanded.
【0016】すなわち、基材についてはTi−Alを主
とするTi−Al系金属間化合物によって充分な高温強
度や耐クリープ強度を発揮し、基材の耐摩耗性が必要な
部位についてはTiの浸透拡散により、Ti3Alを主
とするTiAl系金属間化合物からなる耐摩耗層が形成
され、充分な耐摩耗性を発揮する。That is, a Ti-Al intermetallic compound mainly composed of Ti-Al exerts sufficient high-temperature strength and creep resistance on the base material, and Ti is used on the part where the wear resistance of the base material is required. By permeation and diffusion, a wear resistant layer made of a TiAl-based intermetallic compound mainly composed of Ti 3 Al is formed, and sufficient wear resistance is exhibited.
【0017】本発明においては、表面改質部厚さは5〜
1000μmとすることが好ましい。Ti拡散層の厚さ
が5μm未満では表面改質効果が充分でなく、逆に10
00μmを越えると処理に長時間を要し表面改質層が剥
離するおそれがあるからである。In the present invention, the thickness of the surface modified portion is 5 to 5.
The thickness is preferably 1000 μm. If the thickness of the Ti diffusion layer is less than 5 μm, the surface modification effect is not sufficient, and conversely 10
This is because if it exceeds 00 μm, it takes a long time for the treatment and the surface-modified layer may peel off.
【0018】処理粉末のTi粉末混合量を10〜60重
量%としたのは、10%未満では充分な厚さの表面改質
層が得られないからであり、60%を越えると処理粉末
が焼結しTiの拡散ができなくなり却って表面改質層の
厚さが激減するからである。The amount of the Ti powder mixed in the treated powder is set to 10 to 60% by weight because if the amount is less than 10%, the surface-modified layer having a sufficient thickness cannot be obtained. This is because sintering causes the diffusion of Ti to be impossible and the thickness of the surface modification layer is greatly reduced.
【0019】また、活性化剤である塩化アンモニウムや
フッ化アルミニウム等のハロゲン化物の添加量を10%
以下としたのは、添加量が10%を越えるとTiの拡散
浸透量が却って減少するからである。セラミック粉末は
処理温度でのTi粉末の焼結を防止する作用をする。従
って、セラミック粉末は処理温度で分解やそれ自身の焼
結がないもの、例えば安定酸化物等を用いるのが好まし
く、さらに好ましくはAl203、ZrO2等である。Further, the amount of the activator such as ammonium chloride or aluminum fluoride added is 10%.
The reason why the content is set below is that the diffusion and permeation amount of Ti is rather reduced when the addition amount exceeds 10%. The ceramic powder acts to prevent sintering of the Ti powder at the processing temperature. Therefore, it is preferable to use a ceramic powder that does not decompose or sinter itself at the treatment temperature, for example, a stable oxide, and more preferably Al 2 O 3 or ZrO 2 .
【0020】Tiの拡散浸透処理温度を700〜110
0℃の温度域とし、処理時間を2〜20時間としたの
は、処理条件が700℃未満で2時間未満であると、拡
散速度が遅く充分な処理厚さが得られないからであり、
処理温度が1100℃を越えるとTi−Alの基材の変
態により組織が変わるおそれがあるからであり、処理時
間が20時間を越えても拡散Ti含有量が飽和し、それ
以上増加しないからである。The diffusion and infiltration treatment temperature of Ti is 700 to 110.
The reason why the temperature range is 0 ° C. and the treatment time is 2 to 20 hours is that if the treatment conditions are less than 700 ° C. and less than 2 hours, the diffusion rate is slow and a sufficient treatment thickness cannot be obtained.
This is because if the treatment temperature exceeds 1100 ° C., the structure may change due to the transformation of the Ti—Al base material, and even if the treatment time exceeds 20 hours, the diffused Ti content is saturated and does not increase further. is there.
【0021】Tiを拡散させたTi−Al系合金からな
る基材の加熱処理時間を700〜1100℃で10〜5
0時間としたのは、温度については前記拡散浸透処理と
同じであり、時間については、50時間を越えると部材
に歪みが生じ、面粗度が悪くなるからであり、10時間
未満ではTi拡散の効果が得られないからである。The heat treatment time of the base material made of a Ti-Al type alloy in which Ti is diffused is 700 to 1100 ° C. for 10 to 5 hours.
The time is set to 0 hour because the temperature is the same as that of the diffusion infiltration treatment, and when the time exceeds 50 hours, the member is distorted and the surface roughness deteriorates. This is because the effect of is not obtained.
【0022】[0022]
【実施例】本発明の実施例を説明し本発明の効果を明ら
かにする。 (実施例1)試料No.1として、φ10×10mmの
円柱形状のTi−Al合金(Ti−34重量%Al)を
アルミナ製ルツボに入れ、その周囲を下記組成の拡散剤
粉末にて覆った。この状態でアルゴン雰囲気にした高温
炉内にセットし、950℃にて10時間保持した。EXAMPLES Examples of the present invention will be described to clarify the effects of the present invention. (Example 1) Sample No. As No. 1, a columnar Ti—Al alloy (Ti—34 wt% Al) with a diameter of 10 × 10 mm was placed in an alumina crucible, and the periphery thereof was covered with a diffusing agent powder having the following composition. In this state, it was set in a high temperature furnace in an argon atmosphere and kept at 950 ° C. for 10 hours.
【0023】 (拡散剤処理粉末組成) Ti粉末(80〜200メッシュ) 50重量% 塩化アンモニウム粉末(−275メッシュ) 2重量% Al2O3粉末(80〜200メッシュ) 48重量%(Diffusing agent-treated powder composition) Ti powder (80 to 200 mesh) 50% by weight Ammonium chloride powder (-275 mesh) 2% by weight Al 2 O 3 powder (80 to 200 mesh) 48% by weight
【0024】試料No.2として、試料No.1と同様
にTi拡散浸透処理したφ10×10mmの円柱形状の
TiAl合金(Ti−34重量%Al)をアルミナ製ル
ツボより取り出し、周囲に付着した粉末を除去し、表面
をトリクロロエタン等の有機洗浄剤で洗浄した。この試
料No.2をアルゴン雰囲気にした炉中にセットし、1
100℃にて20時間保持する加熱処理を施した。Sample No. 2, the sample No. A cylindrical TiAl alloy (Ti-34 wt% Al) of φ10 × 10 mm that has been subjected to Ti diffusion and penetration treatment in the same manner as in 1 was taken out from the alumina crucible, the powder adhering to the periphery was removed, and the surface was washed with an organic cleaning agent such as trichloroethane. Washed with. This sample No. Place 2 in a furnace with an argon atmosphere and set 1
A heat treatment of holding at 100 ° C. for 20 hours was performed.
【0025】上記処理にて得られた試料No.1および
No.2を切断し、その断面組織の観察を行った。処理
層厚さを測定したところ、No.1では10μmであっ
た。しかし、No.2では膜と母材との界面が明確でな
く組織の違いによる膜厚判定は困難であった。Sample No. obtained by the above treatment 1 and No. 2 was cut and the cross-sectional structure was observed. When the treatment layer thickness was measured, No. In No. 1, it was 10 μm. However, no. In No. 2, the interface between the film and the base material was not clear, and it was difficult to determine the film thickness due to the difference in structure.
【0026】次に、X線回折によって、処理層の同定を
行った、その結果、母材および処理層No.1、No.
2について、それぞれ下記の化合物が検出された。 母材 : Ti3Al、 TiAl (下線は強い
ピークを示す) No.1: Ti3Al、 TiAl (下線は強い
ピークを示す) No.2: Ti3Al、 TiAl (下線は強い
ピークを示す) ここで、処理層においては、Ti3Alのピークが強く
検出されている。TiAl合金はTiAlとTi3Al
より構成されており、試料No.1およびNo.2の処
理層は、この混合比がTi3Alがリッチになったもの
であることが上記の結果より推定された。Next, the treated layer was identified by X-ray diffraction. As a result, the base material and the treated layer No. 1, No.
The following compounds were detected for 2 respectively. Base material: Ti 3 Al, TiAl (underline shows a strong peak) No. 1: Ti 3 Al, TiAl (underline shows a strong peak) No. 2: Ti 3 Al, TiAl (underline shows a strong peak) Here, the peak of Ti 3 Al is strongly detected in the treated layer. TiAl alloy is TiAl and Ti 3 Al
Sample No. 1 and No. It was estimated from the above results that the treatment ratio of No. 2 was such that the mixture ratio was rich in Ti 3 Al.
【0027】処理層の組成を明確にするために、EPM
Aライン分析によって、Al濃度分布を調査した。その
結果を図1に示す。図1に示す通り拡散浸透処理のみを
施した試料No.1では、処理層界面部でAl含有率が
急激に変化している。また、処理層のAl含有率が28
重量%であることから、処理層の大部分はTi3Alよ
り構成されていることが推定された。In order to clarify the composition of the treatment layer, the EPM
The Al concentration distribution was investigated by A line analysis. The result is shown in FIG. As shown in FIG. 1, the sample No. subjected to only the diffusion and penetration treatment. In No. 1, the Al content changes rapidly at the interface of the treatment layer. Further, the Al content of the treated layer is 28
Since the content was wt%, it was estimated that most of the treated layer was composed of Ti 3 Al.
【0028】一方、拡散処理後に熱処理を行った試料N
o.2では、Al含有率が連続的に変化していることが
わかる。これは、熱処理によって表面近傍のTiが内部
にまで拡散し、その結果、Ti3AlとTiAlとの混
合比が変化したためと推定された。On the other hand, sample N which was heat-treated after the diffusion treatment
o. In No. 2, it can be seen that the Al content changes continuously. This was presumed to be because Ti near the surface was diffused to the inside by the heat treatment, and as a result, the mixing ratio of Ti 3 Al and TiAl was changed.
【0029】(実施例2)拡散処理粉末のTi含有量が
処理層厚さに及ぼす影響について調査するため、Ti含
有量を5〜100重量%の範囲で混合した拡散処理粉末
を用い、実施例1と同様の方法および条件で、Ti−A
l合金にTi拡散処理を施し、Tiが拡散した処理層の
厚さを測定した。その結果を図2に示す。(Example 2) In order to investigate the effect of the Ti content of the diffusion-treated powder on the thickness of the treatment layer, the diffusion-treated powder in which the Ti content was mixed in the range of 5 to 100% by weight was used. In the same method and conditions as in No. 1, Ti-A
The Ti alloy was subjected to Ti diffusion treatment, and the thickness of the treated layer in which Ti was diffused was measured. The result is shown in FIG.
【0030】図2に示したように、処理粉末中のTi含
有量が10重量%以下では、急激に処理層厚さが減少し
ている。これは、母材に対してTi粉末が充分に接して
いないために、拡散原料であるTiが不足したためであ
る。一方、80重量%以上では処理粉末が焼結してしま
い、処理粉末が母材と接合してしまったため、試料の取
り出しが出来なくなった。また、70重量%では試料の
取り出しは出来たものの、処理層の厚さが激減した。こ
れは、処理粉末の一部に焼結が起こり、これにより充分
なTi供給ができなくなったためである。以上の結果よ
り、処理粉末中のTi含有量を10〜60重量%で処理
すると、所望の処理層厚さでTiを拡散浸透させること
ができることが確認された。As shown in FIG. 2, when the Ti content in the treated powder is 10% by weight or less, the treated layer thickness is rapidly reduced. This is because the Ti powder, which is a diffusion raw material, was insufficient because the Ti powder was not in sufficient contact with the base material. On the other hand, when the content is 80% by weight or more, the treated powder was sintered and the treated powder was bonded to the base material, so that the sample could not be taken out. At 70% by weight, although the sample could be taken out, the thickness of the treated layer was drastically reduced. This is because a part of the treated powder was sintered, which made it impossible to supply Ti sufficiently. From the above results, it was confirmed that when the Ti content in the treated powder was treated at 10 to 60% by weight, Ti could be diffused and permeated with a desired treatment layer thickness.
【0031】(実施例3)実施例1と同様な母材および
処理粉末を用い、処理温度、時間を表1に示す通りに変
化させて拡散処理を行い、処理層厚さを測定した。その
結果も併せて表1に示した。なお、表1において、N
o.1は拡散処理温度が低い比較例、No.5は拡散処
理時間の短い比較例、No.9は拡散処理後の熱処理温
度が低い比較例、No.13は拡散処理後の熱処理時間
が短い比較例、No.16は拡散処理後の熱処理時間が
長い比較例である。Example 3 Using the same base material and treated powder as in Example 1, the treatment temperature and time were changed as shown in Table 1 to carry out diffusion treatment, and the treatment layer thickness was measured. The results are also shown in Table 1. In Table 1, N
o. No. 1 is a comparative example in which the diffusion treatment temperature is low, and No. 1 No. 5 is a comparative example having a short diffusion processing time. No. 9 is a comparative example in which the heat treatment temperature after the diffusion treatment is low, and No. 9 No. 13 is a comparative example in which the heat treatment time after the diffusion treatment is short, No. 13 Reference numeral 16 is a comparative example in which the heat treatment time after the diffusion treatment is long.
【0032】[0032]
【表1】 [Table 1]
【0033】表1に示したように、No.1の拡散処理
温度が低い比較例およびNo.5の拡散処理時間の短い
比較例はTiが充分に拡散せず、処理層厚さが2〜3μ
mと薄かった。また、No.9の拡散処理後の熱処理温
度が低い比較例およびNo.13の拡散処理後の熱処理
時間が短い比較例は、共に処理層のTi拡散が不十分
で、処理層の厚さは13μmであった。一方、拡散処理
後の熱処理時間が70時間と長かった比較例No.16
は、母材に歪みが生じ表面粗度が大きくなった。As shown in Table 1, No. No. 1 of the comparative example having a low diffusion treatment temperature and No. In Comparative Example 5 in which the diffusion treatment time was short, Ti did not diffuse sufficiently and the treatment layer thickness was 2 to 3 μm.
It was as thin as m. In addition, No. No. 9 in which the heat treatment temperature after the diffusion treatment is low and No. In Comparative Example 13 in which the heat treatment time after the diffusion treatment was short, the diffusion of Ti in the treatment layer was insufficient and the thickness of the treatment layer was 13 μm. On the other hand, Comparative Example No. 1 in which the heat treatment time after the diffusion treatment was as long as 70 hours. 16
, The base material was distorted and the surface roughness became large.
【0034】これに対して本発明の実施例は、所望の処
理層厚さが得られることが判明し、拡散浸透処理条件
は、処理温度は700〜1100℃の温度域とし、処理
時間は2〜20時間とすることが好ましく、また拡散処
理後の加熱処理は700〜1100℃で10〜50時間
とすることが必要であることが確認された。On the other hand, in the examples of the present invention, it was found that the desired treatment layer thickness was obtained, and the diffusion permeation treatment conditions were such that the treatment temperature was 700 to 1100 ° C. and the treatment time was 2 It was confirmed that the heat treatment is preferably -20 hours, and the heat treatment after the diffusion treatment needs to be 700-1100 ° C for 10-50 hours.
【0035】(実施例4)実施例1の試料No.2につ
いて、その断面の硬度分布を測定し、その結果をAl含
有率との関係図として図3にまとめて示した。図3より
明らかなように、Al含有率が増加するに伴い、つまり
表面から内部に移るのに伴って、硬度は低下しているこ
とがわかる。これは、Ti3AlとTiAlとの混合比
に起因するものであり、Ti3Alの硬度が約400H
v、TiAlの硬度が約200Hvであることにより、
説明できる。(Example 4) Sample No. 1 of Example 1 For No. 2, the hardness distribution of the cross section was measured, and the results are shown together in FIG. 3 as a relational diagram with the Al content. As is clear from FIG. 3, the hardness decreases as the Al content increases, that is, as it moves from the surface to the inside. This is due to the mixing ratio of Ti 3 Al and TiAl, and the hardness of Ti 3 Al is about 400H.
Since the hardness of v and TiAl is about 200 Hv,
I can explain.
【0036】(実施例5)実施例1で作製した試料N
o.1およびNo.2の処理層の摩耗試験を実施した。
摩耗試験は図4に示すように、試料の処理層に、SS4
1からなるリングを、荷重2〜12kgの間で変化させ
て押圧し、回転数200rpmで30分回転し、処理層
の摩耗量mm3を測定し、得られた結果を図5に示し
た。なお、比較のために無処理品およびPVDによるT
iNコーティング品(膜厚5μm)についても、同様に
摩耗試験を行い、図5に併せて示した。(Example 5) Sample N prepared in Example 1
o. 1 and No. Abrasion test of two treated layers was performed.
As shown in FIG. 4, the wear test was performed on the treated layer of the sample with SS4.
The ring consisting of 1 was pressed under a load of 2 to 12 kg, rotated at a rotation speed of 200 rpm for 30 minutes, and the abrasion amount mm 3 of the treated layer was measured. The obtained results are shown in FIG. For comparison, untreated product and PVD-based T
The iN-coated product (film thickness: 5 μm) was similarly subjected to the abrasion test, and the results are also shown in FIG.
【0037】本発明品である試料No.1およびNo.
2共に、低荷重では無処理品に比べて優れた耐摩耗性を
示した。一方、高荷重域においては、試料No.1の摩
耗量がやや増加したものの、試料No.1およびNo.
2共に、低荷重では無処理品およびPVDによるTiN
コーティング品に比べて、優れた耐摩耗性を示した。こ
の結果、本発明の効果が確認されると共に、No.1の
摩耗量が高荷重においてやや高かった理由が、膜厚がN
o.1では10μmと薄いことに起因するものであり、
このような高荷重域での使用に際しては、No.2のよ
うな熱処理による処理層の拡大処理を行うのが好ましい
ことが判明した。Sample No. which is the product of the present invention. 1 and No.
Both of them exhibited excellent wear resistance at low load as compared with the untreated product. On the other hand, in the high load range, the sample No. Although the wear amount of Sample No. 1 increased slightly, Sample No. 1 and No.
Both are untreated under low load and TiN by PVD
It showed superior wear resistance compared to the coated product. As a result, the effect of the present invention was confirmed, and No. The reason why the wear amount of No. 1 was slightly high under high load is that the film thickness is N
o. 1 is due to the thinness of 10 μm,
When using in such a high load range, No. It has been found that it is preferable to perform the treatment of enlarging the treatment layer by heat treatment such as 2.
【0038】(実施例6)本発明の実機評価を行うた
め、TiAl合金(Ti−34重量%Al)を用いて、
自動車エンジン用ピストンピンを作製し、実施例1で示
したと同一条件でNo.1についてはTi拡散浸透処理
を施し、No.2についてはTi拡散浸透処理後さらに
熱処理を施した。また、比較のために、無処理品および
PVDによるTiNコーティング品についても、同様の
ピストンピンを作製した。(Embodiment 6) In order to evaluate the actual equipment of the present invention, a TiAl alloy (Ti-34 wt% Al) was used.
A piston pin for an automobile engine was manufactured and No. 1 was produced under the same conditions as those shown in Example 1. No. 1 was subjected to Ti diffusion and infiltration treatment, and No. 1 was used. Regarding No. 2, after the Ti diffusion and infiltration treatment, further heat treatment was performed. Also, for comparison, similar piston pins were prepared for the untreated product and the PVD TiN-coated product.
【0039】これらピストンピンを、3l−8気筒エン
ジンに組み込み、実機評価を行った。評価条件は、〔過
吸圧650mmHgでの4000rpm全負荷運転6
分〕→〔アイドル運転1分〕→〔停止6分〕→〔アイド
ル運転1分〕を1サイクルとし、このサイクルを繰り返
し、摩耗または異常の有無で評価した。得られた結果は
表2にまとめて示した。These piston pins were incorporated into a 3l-8 cylinder engine and the actual machine was evaluated. The evaluation conditions are: 4000 rpm full load operation 6 with over-absorption pressure of 650 mmHg.
Minutes → [Idle operation 1 minute] → [Stop 6 minutes] → [Idle operation 1 minute] was set as one cycle, and this cycle was repeated to evaluate whether there was wear or abnormality. The results obtained are summarized in Table 2.
【0040】[0040]
【表2】 [Table 2]
【0041】表2に示したように、無処理品は100時
間で摩耗し150時間で運転を中止した。また、PVD
(TiNコーティング)品は150時間で摩耗が始まり
250時間までしか運転できなかった。これに対して本
発明品は優れた性能を発揮し、目標値である500時間
をクリヤーする性能であって、本発明の効果が確認され
た。As shown in Table 2, the untreated product was worn out in 100 hours and stopped in 150 hours. Also PVD
The (TiN coated) product started to wear at 150 hours and could only be operated for up to 250 hours. On the other hand, the product of the present invention exhibited excellent performance and was the performance of clearing the target value of 500 hours, and the effect of the present invention was confirmed.
【0042】[0042]
【発明の効果】本発明のTi−Al系合金部材へのTi
拡散浸透処理方法は以上詳述したように、Ti−Al系
合金からなる基材を、チタン粉末に活性化剤粉末および
焼結防用の安定酸化物を混合した処理粉末で覆い、不活
性雰囲気中で加熱して、Tiを拡散させ、必要に応じて
さらに不活性雰囲気中で、700〜1100℃で10〜
50時間の加熱処理を行うことを特徴とするものであっ
て、Ti−Al系合金部材は処理粉末中で熱処理してT
iを拡散浸透させるので、処理面積の大きな部材でも、
また複雑形状の部材であっても、処理が可能であり、耐
摩耗性に優れたTi−Al系合金部材が得られ、さら
に、加熱処理を行うことにより、Tiがより深部まで拡
散浸透して、耐摩耗性のある拡散深さが拡大される。EFFECTS OF THE INVENTION Ti applied to the Ti--Al alloy member of the present invention
As described in detail above, the diffusion permeation treatment method is performed by covering a base material made of a Ti-Al alloy with a treated powder in which titanium powder is mixed with an activator powder and a stable oxide for sintering prevention, and an inert atmosphere is used. Heating in an atmosphere to diffuse Ti and, if necessary, further in an inert atmosphere at 700 to 1100 ° C. for 10 to 10
The heat treatment is performed for 50 hours, and the Ti-Al alloy member is heat treated in the treated powder to obtain T
Since i is diffused and permeated, even for members with a large processing area,
Further, even a member having a complicated shape can be processed, and a Ti-Al alloy member excellent in wear resistance can be obtained. Further, by heat treatment, Ti diffuses and penetrates to a deeper portion. The diffusion depth with wear resistance is expanded.
【図面の簡単な説明】[Brief description of drawings]
【図1】本発明方法により処理した処理層の表面からの
距離とAl含有量との関係を示した線図である。FIG. 1 is a diagram showing the relationship between the distance from the surface of a treated layer treated by the method of the present invention and Al content.
【図2】処理粉末中のTi含有量と処理層厚さとの関係
を示す線図である。FIG. 2 is a diagram showing the relationship between the Ti content in the treated powder and the treated layer thickness.
【図3】本発明方法で処理された処理層のAl含有量と
硬度の関係を示す線図である。FIG. 3 is a diagram showing a relationship between Al content and hardness of a treated layer treated by the method of the present invention.
【図4】摩耗試験の試験方法を説明する斜視図である。FIG. 4 is a perspective view illustrating a test method of a wear test.
【図5】摩耗試験における荷重と摩耗量との関係を示す
線図である。FIG. 5 is a diagram showing a relationship between a load and a wear amount in a wear test.
Claims (2)
比で10〜60wt%のチタン粉末と、10wt%以下
のハロゲン化合物と、残部がセラミック粉末からなる処
理粉末で覆い、不活性雰囲気中で加熱して、Tiを拡散
させることを特徴とするTi−Al系合金部材へのTi
拡散浸透処理方法。1. A base material made of a Ti--Al alloy is covered with a treated powder having a mixing ratio of 10 to 60 wt% titanium powder, 10 wt% or less of a halogen compound, and the balance being ceramic powder, and an inert atmosphere. Ti in a Ti-Al based alloy member characterized by heating in an atmosphere to diffuse Ti
Diffusion and penetration treatment method.
なる基材を、前記処理粉末から取り出し、さらに不活性
雰囲気中で、700〜1100℃で10〜50時間の加
熱処理を行うことを特徴とする請求項1に記載のTi−
Al系合金部材へのTi拡散浸透処理方法。2. A base material made of a Ti—Al-based alloy in which Ti is diffused is taken out from the treated powder, and further heat-treated at 700 to 1100 ° C. for 10 to 50 hours in an inert atmosphere. Ti- according to claim 1, characterized in that
A method for diffusing and permeating Ti into an Al-based alloy member.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP18706092A JPH0633221A (en) | 1992-07-14 | 1992-07-14 | Ti cementation method of ti-al based alloy member |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP18706092A JPH0633221A (en) | 1992-07-14 | 1992-07-14 | Ti cementation method of ti-al based alloy member |
Publications (1)
Publication Number | Publication Date |
---|---|
JPH0633221A true JPH0633221A (en) | 1994-02-08 |
Family
ID=16199462
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP18706092A Pending JPH0633221A (en) | 1992-07-14 | 1992-07-14 | Ti cementation method of ti-al based alloy member |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH0633221A (en) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US5813917A (en) * | 1995-05-12 | 1998-09-29 | Toyota Motor Co Ltd | Shaft assembly |
CN105925934A (en) * | 2016-06-11 | 2016-09-07 | 芜湖众源复合新材料有限公司 | Heating and setting device for surface treatment of arc-shaped bolts |
-
1992
- 1992-07-14 JP JP18706092A patent/JPH0633221A/en active Pending
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US5813917A (en) * | 1995-05-12 | 1998-09-29 | Toyota Motor Co Ltd | Shaft assembly |
CN105925934A (en) * | 2016-06-11 | 2016-09-07 | 芜湖众源复合新材料有限公司 | Heating and setting device for surface treatment of arc-shaped bolts |
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