JPH0372057A - Structural member made of titanium or titanium alloy - Google Patents
Structural member made of titanium or titanium alloyInfo
- Publication number
- JPH0372057A JPH0372057A JP20945389A JP20945389A JPH0372057A JP H0372057 A JPH0372057 A JP H0372057A JP 20945389 A JP20945389 A JP 20945389A JP 20945389 A JP20945389 A JP 20945389A JP H0372057 A JPH0372057 A JP H0372057A
- Authority
- JP
- Japan
- Prior art keywords
- titanium
- surface layer
- structural member
- phase
- titanium alloy
- 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
- 239000010936 titanium Substances 0.000 title claims abstract description 18
- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 16
- 229910052719 titanium Inorganic materials 0.000 title claims abstract description 13
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 title claims abstract description 12
- 239000002344 surface layer Substances 0.000 claims abstract description 29
- 239000000463 material Substances 0.000 claims abstract description 19
- 230000008018 melting Effects 0.000 claims abstract description 17
- 238000002844 melting Methods 0.000 claims abstract description 17
- 238000005275 alloying Methods 0.000 claims abstract description 10
- 230000004048 modification Effects 0.000 claims abstract description 8
- 238000012986 modification Methods 0.000 claims abstract description 8
- 239000002245 particle Substances 0.000 claims description 20
- 229910052751 metal Inorganic materials 0.000 claims description 12
- 239000002184 metal Substances 0.000 claims description 12
- 238000000034 method Methods 0.000 claims description 4
- 239000000843 powder Substances 0.000 abstract description 12
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 abstract description 10
- 229910002092 carbon dioxide Inorganic materials 0.000 abstract description 5
- 239000001569 carbon dioxide Substances 0.000 abstract description 5
- 229910003178 Mo2C Inorganic materials 0.000 abstract 1
- 239000000853 adhesive Substances 0.000 abstract 1
- 230000001070 adhesive effect Effects 0.000 abstract 1
- 239000010953 base metal Substances 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 11
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 11
- 239000000956 alloy Substances 0.000 description 6
- 229910045601 alloy Inorganic materials 0.000 description 5
- 229910052799 carbon Inorganic materials 0.000 description 4
- 239000007789 gas Substances 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 239000010419 fine particle Substances 0.000 description 2
- 239000010410 layer Substances 0.000 description 2
- 150000001247 metal acetylides Chemical class 0.000 description 2
- 238000005240 physical vapour deposition Methods 0.000 description 2
- 238000004881 precipitation hardening Methods 0.000 description 2
- 238000007712 rapid solidification Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 229910000669 Chrome steel Inorganic materials 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000001307 helium Substances 0.000 description 1
- 229910052734 helium Inorganic materials 0.000 description 1
- SWQJXJOGLNCZEY-UHFFFAOYSA-N helium atom Chemical compound [He] SWQJXJOGLNCZEY-UHFFFAOYSA-N 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 230000031700 light absorption Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 230000013011 mating Effects 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000007747 plating Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
Landscapes
- Valve-Gear Or Valve Arrangements (AREA)
Abstract
Description
【発明の詳細な説明】 Ａ１発明の目的 （１）産業上の利用分野 本発明はチタンまたはチタン合金製構造部材に関する。[Detailed description of the invention] A1 Purpose of the invention (1) Industrial application fields The present invention relates to structural members made of titanium or titanium alloys.
（２）従来の技術
従来、この種構造部材として、その摺動特性要求部位に
、金属溶射層、複合メツキ層、化学蒸着膜（ＣＶＤ）
、物理蒸着膜（ＰＶＤ）等の皮膜を形成したものが知ら
れている。(2) Conventional technology Conventionally, this type of structural member has been coated with metal sprayed layers, composite plating layers, and chemical vapor deposited films (CVD) in areas that require sliding properties.
, physical vapor deposition (PVD) films, etc. are known.
（３）発明が解決しようとする課題
しかしながら、従来の構造部材は、通常の摺動条件下で
の使用には耐えることができるとしても、高速、且つ高
面圧下で使用すると、前記皮膜および母材間の密着が破
断されて、その皮膜が剥離する、といった不具合を生じ
るおそれがある。(3) Problems to be Solved by the Invention However, although conventional structural members can withstand use under normal sliding conditions, when used at high speeds and under high surface pressure, the coating and matrix There is a risk of problems such as the adhesion between the materials being broken and the film peeling off.
本発明は前記に鑑み、素材の表面に改質処理を施すこと
により、母材との密着力が高く、且つ優れた摺動特性お
よび強度を持つ表層部を備えた前記構造部材を提供する
ことを目的とする。In view of the above, it is an object of the present invention to provide the above-mentioned structural member, which has a surface layer portion that has high adhesion to the base material and has excellent sliding characteristics and strength by subjecting the surface of the material to a modification treatment. With the goal.
Ｂ１発明の構成
（１） 課題を解決するための手段
本発明は、金属組織がα相またはα＋β相であるチタン
またはチタン合金よりなる素材の表面に、改質処理を施
して形成された表層部を有するチタンまたはチタン合金
製構造部材であって、前記表層部は、前記改質処理とし
て高密度エネルギ源を用いた局所溶融合金化処理により
得られると共に金属組織がβ相であることを特徴とする
。B1 Structure of the Invention (1) Means for Solving the Problem The present invention provides a surface layer portion formed by performing a modification treatment on the surface of a material made of titanium or a titanium alloy whose metal structure is α phase or α+β phase. A structural member made of titanium or titanium alloy, wherein the surface layer portion is obtained by local melting alloying treatment using a high-density energy source as the modification treatment, and the metal structure is β phase. do.
（２）作 用
前記局所溶融合金化処理を適用すると、溶融径自己冷却
による急速凝固作用が得られるので、表層部の金属組織
が微細で、且つ均質となり、また表層部の金属組織がβ
相となっているので、その表層部の摺動特性および強度
が向上する。(2) Effect When the above-mentioned local melting alloying treatment is applied, a rapid solidification effect is obtained by self-cooling of the melt diameter, so the metal structure in the surface layer becomes fine and homogeneous, and the metal structure in the surface layer becomes β.
Since it is a phase, the sliding characteristics and strength of the surface layer are improved.
その上、前記局所熔融合金化処理による表層部は、母材
としてのチタンまたはチタン合金に対する密着力が強く
、高速、且つ高面圧下での摺動に際し、剥離するような
ことはない。Furthermore, the surface layer formed by the local melting and alloying treatment has strong adhesion to titanium or a titanium alloy as a base material, and does not peel off when sliding at high speed and under high surface pressure.
（３）実施例
第１図はチタン合金製構造部材としてのロッカアームｌ
を示す。ロッカアーム１は内燃機関用動弁機構に用いら
れるもので、その一端部にカムと摺擦するスリッパ面２
を有する。(3) Example Figure 1 shows a rocker arm l as a titanium alloy structural member.
shows. A rocker arm 1 is used in a valve mechanism for an internal combustion engine, and has a slipper surface 2 at one end that rubs against a cam.
has.
ロッカアームｌの製造に当っては、金属組織がα＋β相
であり、且つＴｉ−６Ａｆ−４Ｖの組成を持つα＋β型
チタン合金製素材が用いられ、スリッパ面２を構成する
表層部３は、素材表面に高密度エネルギ源を用いた局所
溶融合金化処理を施して改質されたものである。In manufacturing the rocker arm 1, an α+β type titanium alloy material with a metal structure of α+β phase and a composition of Ti-6Af-4V is used, and the surface layer 3 constituting the slipper surface 2 is It is modified by applying local melting alloying treatment using a high-density energy source.
高密度エネルギ源としては、炭酸ガスレーザが適用され
、また合金化に際し、Ｍｏ、Ｃ粉末およびＦｅ粉末が用
いられる。A carbon dioxide laser is used as a high-density energy source, and Mo, C powder, and Fe powder are used for alloying.
したがって、表層部３の金属組織はβ相であり、また１
５〜３０重量％のＭｏと、５〜１０重量％のＦｅを含有
し、さらに硬質粒子として体積分率（Ｖｆ）１０〜３０
％のＴｉｃ粒子を含有している。Therefore, the metal structure of the surface layer 3 is β phase, and 1
Contains 5 to 30% by weight of Mo and 5 to 10% by weight of Fe, and further has a volume fraction (Vf) of 10 to 30 as hard particles.
% of Tic particles.
Ｍｏは、全率固溶型β安定化元素であって、母材である
前記α＋β型チタン合金と全率固溶体をつくる。Ｍｏを
１５重量％以上含有させることによって、β相を室温ま
で持ちきたすことができる。Mo is a completely solid solution β-stabilizing element, and forms a completely solid solution with the α+β type titanium alloy that is the base material. By containing Mo in an amount of 15% by weight or more, the β phase can be brought to room temperature.
またＭｏはβ相の摺動特性および耐熱性を向上させ、そ
の上、ＦｅをＴｉと合金化し易くするといった効果を有
する。Mo also has the effect of improving the sliding properties and heat resistance of the β phase, and also making it easier to alloy Fe with Ti.
これらの効果は、Ｍｏの含有量が３０重量％を上回って
も変わらないので、その含有量の上限は３０重量％に設
定される。These effects remain unchanged even if the Mo content exceeds 30% by weight, so the upper limit of the content is set at 30% by weight.
た℃°シ、Ｍｏの単独添加では、β相の硬さが低く、高
面圧下における十分な耐摩耗性が得られない。However, when Mo is added alone, the hardness of the β phase is low and sufficient wear resistance under high surface pressure cannot be obtained.
Ｆｅは共析型β安定化元素である。Ｆｅを５重量％以上
含有させることによって、β相の安定化が図られ、また
析出硬化作用を生じさせてβ相の硬さ、したがって耐摩
耗性を向上させることができる。Fe is a eutectoid β-stabilizing element. By containing Fe in an amount of 5% by weight or more, the β phase can be stabilized, and a precipitation hardening effect can be caused to improve the hardness of the β phase and therefore the wear resistance.
たくし、Ｆｅの含有量が１０重量％を上回ると、ＦｅＯ
固溶性が低いことに起因して、偏析等を生じ、安定した
β相が得られなくなる。したがって、Ｆｅ含有量の上限
は１０重量％に設定される。When the Fe content exceeds 10% by weight, FeO
Due to the low solid solubility, segregation etc. occur, making it impossible to obtain a stable β phase. Therefore, the upper limit of the Fe content is set to 10% by weight.
なお、Ｍｏを添加せずに、Ｆｅのみを添加すると、前記
析出硬化作用に伴い金属間化合物が形成されて表層部が
脆化する傾向にあるが、この問題はＭｏを併用すること
によって解消される。Note that if only Fe is added without adding Mo, intermetallic compounds are formed due to the precipitation hardening effect and the surface layer tends to become brittle, but this problem can be resolved by using Mo in combination. Ru.
ＴｉＣ粒子は、合金化に際し、Ｍｏ、Ｃ−＋２Ｍｏ ＋
Ｃ，Ｔ ｉ ＋Ｃ−＋Ｔ ｉ Ｃの反応により析出する
もので、表層部３の硬さを確保して、その耐摩耗性を向
上させる効果を有する。During alloying, TiC particles are composed of Mo, C-+2Mo +
It is precipitated by the reaction of C, Ti + C- + Ti C, and has the effect of ensuring the hardness of the surface layer 3 and improving its wear resistance.
また、ＴｉＣ粒子は析出現象により生しるものであるか
ら、１〜５μｍの粒径を有するＶ＆細粉粒子あり、且つ
分散性も良く、その上、粒子形状が丸いので、摺動相手
材の摩耗量を増加させる等の攻撃性が低い、といった利
点を有する。In addition, since TiC particles are produced by a precipitation phenomenon, there are V&fine particles with a particle size of 1 to 5 μm, and they also have good dispersibility.Furthermore, the particle shape is round, so it is suitable for sliding mating materials. It has the advantage of being less aggressive, such as increasing the amount of wear.
一般に、硬質粒子を分散させる場合、前記粒径を得るに
は、必然的に破砕粉を用いることになるが、破砕粉の形
状は角張っていて、砥粒効果を発揮するため摺動相手材
に対する攻撃性が高い、また前記範囲の微小粒径を得る
には、精密分級処理を行わなければならないので、膨大
なコスト上昇を惹起することになる。Generally, when dispersing hard particles, crushed powder is inevitably used to obtain the above-mentioned particle size, but the crushed powder has an angular shape and exhibits an abrasive effect, so In order to obtain particles with high aggressiveness and a fine particle size within the above range, precision classification processing must be performed, resulting in a huge increase in cost.
なお、ＴｉＣ粒子の体積分率が１０％未満では、前記効
果を得ることができず、一方、３０％を上回ると、摺動
相手材への攻撃性が増大し、また表層部３が跪化し、さ
らにＴｉＣ粒子が脱落し易くなる。It should be noted that if the volume fraction of TiC particles is less than 10%, the above effect cannot be obtained, while if it exceeds 30%, the aggressiveness towards the sliding material increases and the surface layer 3 becomes sluggish. , furthermore, the TiC particles tend to fall off.
以下、ロッカアームｌの局所溶融合金化処理について説
明する。Hereinafter, the local melting alloying process of the rocker arm l will be explained.
第２図は、前記処理法を示し、前記母材（Ｔｉ６Ａｆｆ
ｉ−４Ｖ）よりなるロッカアーム用素材１゜を矢印方向
へ移動させ、そのスリッパ面対応部２゜に、オシレータ
５より炭酸ガスレーザを照射し、同時にガス供給ノズル
６よリシールドガスであるヘリウムガスを、また粉末供
給ノズル７よりＭｏ、Ｃ粉末およびＦｅ粉末をそれぞれ
供給するものである。FIG. 2 shows the treatment method and shows the base material (Ti6Aff).
i-4V) is moved in the direction of the arrow, and its slipper surface corresponding portion 2° is irradiated with a carbon dioxide laser from the oscillator 5, and at the same time, helium gas, which is a reshielding gas, is supplied from the gas supply nozzle 6. , Mo powder, C powder, and Fe powder are supplied from the powder supply nozzle 7, respectively.
処理条件は次の通りである。The processing conditions are as follows.
ロッカアーム用素材１０の移動速度（処理速度） ：
３００ ａｍ／＋ｗｉｎ
炭酸ガスレーザ：出力 ５ｋＷ、スポット径２ｍ、振幅
５ｍ、パワー密度 ５〜６Ｘ１０’Ｗ／ｄ
Ｍｏ、Ｃ粉末：直径 １０〜４４μｍ、供給量１５．７
ｇ／＋ｗｉｎ ； Ｆ Ｃ粉末：純度 ９９％以上
、粒度 ２００メツシユ以下、供給Ｎ４．６ｇ／ｉｎ
前記処理により、金属組織がβ相で、ＴｉＣ粒子を分散
させた表層部３が得られる。Movement speed (processing speed) of rocker arm material 10:
300 am/+win Carbon dioxide laser: Output 5kW, spot diameter 2m, amplitude 5m, power density 5~6X10'W/d Mo, C powder: Diameter 10~44μm, supply amount 15.7
g/+win; FC powder: purity 99% or more, particle size 200 mesh or less, supply N 4.6 g/in Through the above treatment, a surface layer 3 having a β phase metallographic structure and having TiC particles dispersed therein is obtained.
炭酸ガスレーザといった高密度エネルギ源による局所溶
融合金化処理においては、溶融接自己冷却による急速凝
固作用が得られるので、金属組織が微細で、且つ均質と
なり、したがって安定した摺動特性および強度が得られ
る。また母材に対する表層部３の密着力も強い。In local melting alloy processing using a high-density energy source such as a carbon dioxide laser, rapid solidification is achieved by self-cooling of the weld, resulting in a fine and homogeneous metal structure, resulting in stable sliding properties and strength. . Furthermore, the adhesion of the surface layer 3 to the base material is strong.
Ｍｏの添加に際し、Ｍｏ、Ｃといった炭化物を用いる理
由は、硬質粒子であるＴｉＣ粒子を析出させることの外
、次に述べるように炭化物の低融点効果を狙ったもので
ある。The reason why carbides such as Mo and C are used when adding Mo is not only to precipitate TiC particles, which are hard particles, but also to aim at the low melting point effect of the carbides, as described below.
即ち、金属ＭＯは、融点が２６１０°Ｃといった高融点
材料であり、そのま覧では、融点が１６６８°Ｃといっ
たチタン合金におけるＴｉとの合金化が難しいが、炭化
物の状態で用いると、その融点が２４００ ”Ｃ程度に
低下するため、Ｔｉとの融点差が小さくなって合金化し
易くなる。また炭化物の粉末は、金属ＭＯに比べて吸熱
能（吸光能）が高く、したがってエネルギ効率上からも
有利である。That is, metal MO is a high melting point material with a melting point of 2610°C, and apparently it is difficult to alloy with Ti in a titanium alloy with a melting point of 1668°C, but when used in the form of a carbide, its melting point is As the melting point difference with Ti decreases to about 2400"C, the difference in melting point with Ti becomes smaller, making it easier to form an alloy. Carbide powder also has a higher endothermic ability (light absorption ability) than metal MO, and therefore is less effective in terms of energy efficiency. It's advantageous.
前記処理により得られた表層部３の＆ｌｌ戒は、Ｔｉ
−２４，４Ｍ ｏ −８，３Ｆ ｅ −３，３Ａ １．
−２．４ Ｖであり、Ｔｉｃ粒子の平均粒径は２．８μ
ｍ、体積分率は１６．８％であった。≪ of the surface layer 3 obtained by the above treatment is Ti
-24,4M o -8,3F e -3,3A 1.
-2.4 V, and the average particle size of Tic particles is 2.8μ
m, the volume fraction was 16.8%.
第３図は、前記表層部３を備えた本発明に係るロッカア
ームＡおよび比較例ロッカアームＢ−Ｄの摺動テスト結
果を示す。FIG. 3 shows the results of a sliding test of rocker arm A according to the present invention and comparative example rocker arm BD, which are provided with the surface layer portion 3.
下表は比較例ロッカアームＢ−Ｄの材質を示す。The table below shows the materials of comparative example rocker arms B-D.
Ｊｆ１例ロッカアームＢにおける表中の材質はチップ材
の材質であって、本体はクロム鋼（ＪＩＳＳＣｒ４１５
）より構成される。The material listed in the table for Jf1 example rocker arm B is the chip material, and the main body is made of chrome steel (JISSCr415
).
摺動テスト結果は、各ロッカアームＡ−Ｄをエンジンに
組込み、Ｐｖ値５４０ｋｇｆ／ｍｍ” ・ｍ／ｓの条
件下でモータリングテストを行い、１時間後のスリッパ
面における摩耗量を測定することによって求められた。The sliding test results were obtained by installing each rocker arm A-D into the engine, conducting a motoring test under the condition of Pv value of 540 kgf/mm'' m/s, and measuring the amount of wear on the slipper surface after 1 hour. I was asked.
第３図から明らかなように、本発明における表層部３は
従来の高Ｃｒ鉄系焼結材性チップ材と路間等の耐摩耗性
を示すことが判る。As is clear from FIG. 3, it can be seen that the surface layer portion 3 of the present invention exhibits wear resistance in the grooves and the like compared to the conventional high Cr iron-based sintered chip material.
なお、本発明は、α型およびα＋β型チタンならびにα
型チタン合金にも適用され、また硬質粒子を含まない表
層部を持つ構造部材を提供することもできる。In addition, the present invention relates to α-type and α+β-type titanium and α
It is also applicable to type titanium alloys, and it is also possible to provide a structural member having a surface layer that does not contain hard particles.
Ｃ０発明の効果
本発明によれば、表層部を得るための改質処理および表
層部の金属組織を前記のように特定することによって、
母材との密着力が高く、且つ優れた摺動特性および強度
を持つ表層部を備えたチタンまたはチタン合金製構造部
材を提供することができる。Effects of the C0 Invention According to the present invention, by specifying the modification treatment for obtaining the surface layer portion and the metal structure of the surface layer portion as described above,
It is possible to provide a titanium or titanium alloy structural member that has a surface layer that has high adhesion to the base material and has excellent sliding properties and strength.
第１図はロッカアームの要部破断正面図、第２図は局所
溶融合金化処理法の説明図、第３図は摺動テスト結果を
示すグラフである。
１・・・ロッカアーム（構造部材）、３・・・表層部第
１図
第２図FIG. 1 is a cutaway front view of the main part of the rocker arm, FIG. 2 is an explanatory diagram of the local melting alloy treatment method, and FIG. 3 is a graph showing the results of a sliding test. 1...Rocker arm (structural member), 3...Surface part Fig. 1 Fig. 2
Claims (3)
はチタン合金よりなる素材の表面に、改質処理を施して
形成された表層部を有する構造部材であって、前記表層
部は、前記改質処理として高密度エネルギ源を用いた局
所溶融合金化処理により得られると共に金属組織がβ相
であることを特徴とするチタンまたはチタン合金製構造
部材。(1) A structural member having a surface layer formed by performing a modification treatment on the surface of a material made of titanium or a titanium alloy whose metallographic structure is an α phase or an α+β phase, the surface layer being 1. A structural member made of titanium or a titanium alloy, which is obtained by a local melting alloying process using a high-density energy source as a quality treatment, and has a metal structure of β phase.
１０重量％のＦｅを含有している、第（１）項記載のチ
タンまたはチタン合金製構造部材。(2) The surface layer portion contains 15 to 30% by weight of Mo and 5 to 30% by weight of Mo.
The titanium or titanium alloy structural member according to item (1), containing 10% by weight of Fe.
、その硬質粒子の体積分率（Ｖｆ）は、１０〜３０％で
ある、第（１）または第（２）項記載のチタンまたはチ
タン合金製構造部材。(3) The titanium according to item (1) or (2), wherein the surface layer portion contains uniformly dispersed hard particles, and the volume fraction (Vf) of the hard particles is 10 to 30%. or titanium alloy structural members.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP20945389A JPH0372057A (en) | 1989-08-11 | 1989-08-11 | Structural member made of titanium or titanium alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP20945389A JPH0372057A (en) | 1989-08-11 | 1989-08-11 | Structural member made of titanium or titanium alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0372057A true JPH0372057A (en) | 1991-03-27 |
Family
ID=16573125
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP20945389A Pending JPH0372057A (en) | 1989-08-11 | 1989-08-11 | Structural member made of titanium or titanium alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0372057A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008514046A (en) * | 2004-09-14 | 2008-05-01 | カー・ウント・ハー・フェアトリープス・ウント・エントヴィックルングスゲゼルシャフト・エムベーハー | Apparatus for receiving audio signals transmitted in a wireless manner |
| JP2010204193A (en) * | 2009-02-27 | 2010-09-16 | Sony Corp | Content reproduction apparatus, content receiving apparatus, method of reproducing content, program, and content reproduction system |
| US8280071B2 (en) | 2004-10-28 | 2012-10-02 | Sony Corporation | Voice output system and method |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6256561A (en) * | 1985-09-06 | 1987-03-12 | Honda Motor Co Ltd | Method for hardening surface of ti or ti alloy |
| JPS62270277A (en) * | 1986-05-18 | 1987-11-24 | Daido Steel Co Ltd | Production of titanium base alloy-made wear resistant member |
| JPS6393875A (en) * | 1986-10-07 | 1988-04-25 | Mitsubishi Heavy Ind Ltd | Production of ti alloy member having superior wear resistance |
-
1989
- 1989-08-11 JP JP20945389A patent/JPH0372057A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6256561A (en) * | 1985-09-06 | 1987-03-12 | Honda Motor Co Ltd | Method for hardening surface of ti or ti alloy |
| JPS62270277A (en) * | 1986-05-18 | 1987-11-24 | Daido Steel Co Ltd | Production of titanium base alloy-made wear resistant member |
| JPS6393875A (en) * | 1986-10-07 | 1988-04-25 | Mitsubishi Heavy Ind Ltd | Production of ti alloy member having superior wear resistance |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008514046A (en) * | 2004-09-14 | 2008-05-01 | カー・ウント・ハー・フェアトリープス・ウント・エントヴィックルングスゲゼルシャフト・エムベーハー | Apparatus for receiving audio signals transmitted in a wireless manner |
| US8280071B2 (en) | 2004-10-28 | 2012-10-02 | Sony Corporation | Voice output system and method |
| JP2010204193A (en) * | 2009-02-27 | 2010-09-16 | Sony Corp | Content reproduction apparatus, content receiving apparatus, method of reproducing content, program, and content reproduction system |
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