JPH0368786A - Structural member made of titanium or titanium alloy - Google Patents
Structural member made of titanium or titanium alloyInfo
- Publication number
- JPH0368786A JPH0368786A JP20428789A JP20428789A JPH0368786A JP H0368786 A JPH0368786 A JP H0368786A JP 20428789 A JP20428789 A JP 20428789A JP 20428789 A JP20428789 A JP 20428789A JP H0368786 A JPH0368786 A JP H0368786A
- Authority
- JP
- Japan
- Prior art keywords
- phase
- titanium
- structural member
- surface layer
- item
- 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
- 229910001069 Ti alloy Inorganic materials 0.000 title claims description 18
- 239000010936 titanium Substances 0.000 title claims description 14
- 229910052719 titanium Inorganic materials 0.000 title claims description 12
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 title claims description 11
- 239000002344 surface layer Substances 0.000 claims abstract description 39
- 239000002245 particle Substances 0.000 claims description 28
- 229910052751 metal Inorganic materials 0.000 claims description 10
- 239000002184 metal Substances 0.000 claims description 10
- 239000000203 mixture Substances 0.000 claims description 4
- 239000000463 material Substances 0.000 abstract description 22
- 239000000843 powder Substances 0.000 abstract description 18
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 abstract description 8
- 239000007789 gas Substances 0.000 abstract description 5
- 239000000956 alloy Substances 0.000 abstract description 4
- 229910002092 carbon dioxide Inorganic materials 0.000 abstract description 4
- 239000001569 carbon dioxide Substances 0.000 abstract description 4
- 229910045601 alloy Inorganic materials 0.000 abstract description 3
- 239000001307 helium Substances 0.000 abstract description 2
- 229910052734 helium Inorganic materials 0.000 abstract description 2
- SWQJXJOGLNCZEY-UHFFFAOYSA-N helium atom Chemical compound [He] SWQJXJOGLNCZEY-UHFFFAOYSA-N 0.000 abstract description 2
- 229910003178 Mo2C Inorganic materials 0.000 abstract 1
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 22
- 238000012986 modification Methods 0.000 description 12
- 230000004048 modification Effects 0.000 description 12
- 230000000694 effects Effects 0.000 description 8
- 230000008018 melting Effects 0.000 description 8
- 238000002844 melting Methods 0.000 description 8
- 238000000034 method Methods 0.000 description 5
- 229910052799 carbon Inorganic materials 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 4
- 101000993059 Homo sapiens Hereditary hemochromatosis protein Proteins 0.000 description 3
- 238000006243 chemical reaction Methods 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 238000005275 alloying Methods 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 230000008014 freezing Effects 0.000 description 2
- 238000007710 freezing Methods 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 239000010687 lubricating oil Substances 0.000 description 2
- 238000001000 micrograph Methods 0.000 description 2
- 238000004881 precipitation hardening Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 229910017263 Mo—C Inorganic materials 0.000 description 1
- 241001125046 Sardina pilchardus Species 0.000 description 1
- 229910000746 Structural steel Inorganic materials 0.000 description 1
- 210000000436 anus Anatomy 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005255 carburizing Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000004453 electron probe microanalysis Methods 0.000 description 1
- 210000002615 epidermis Anatomy 0.000 description 1
- 239000010419 fine particle Substances 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 239000010410 layer Substances 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
- 239000000155 melt Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000007712 rapid solidification Methods 0.000 description 1
- 235000019512 sardine Nutrition 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
Abstract
Description
【発明の詳細な説明】 Ａ０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] A0 Purpose of 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、その部材の摺動特性要求
部位を、金属組織が単一のβ相であるβ型チタン合金よ
り構成したものが知られている（特開昭６１−２４７８
０６号公報参照）。(2) Conventional technology Conventionally, this type of structural member is known in which the portion of the member requiring sliding properties is made of a β-type titanium alloy whose metal structure is a single β phase (Unexamined Japanese Patent Publication No. Showa 61-2478
(See Publication No. 06).
（３）発明が解決しようとする、課題
しかしながら、前記β型チタン合金は、α型およびα＋
β型チタン合金に比べて摺動特性が若干向上するもの＼
、高速、且つ高面圧下で使用される構造部材の要求摺動
特性を満たすことはできない。(3) Problems to be Solved by the Invention However, the β-type titanium alloy is
Slightly improved sliding properties compared to β-type titanium alloys＼
, it cannot satisfy the required sliding characteristics of structural members used at high speeds and under high surface pressure.
本発明は前記に鑑み、金属組織を混在組織にして、優れ
た摺動特性および強度を持つ表層部を備えた前記チタン
またはチタン合金製構造部材を提供することを目的とす
る。In view of the above, an object of the present invention is to provide a structural member made of titanium or a titanium alloy, which has a surface layer having a mixed metal structure and excellent sliding properties and strength.
Ｂ９発明の構成
（１）課題を解決するための手段
本発明に係るチタンまたはチタン合金製構造部材は、表
層部の金属組織が、特性を異にする複数種のβ相を混在
させた組織であることを特徴とする。B9 Structure of the Invention (1) Means for Solving the Problems The titanium or titanium alloy structural member according to the present invention has a metal structure in the surface layer that is a mixture of multiple types of β phases having different characteristics. characterized by something.
（２）作 用
前記のように、表層部において特性を異にする複数種の
β相を混在させると、単一のβ相を有するものに比べて
表層部の摺動特性が大幅に向上し、したがって表層部が
高速、且つ高面圧下においても優れた耐久性を示し、ま
た表層部の強度も大幅に向上する。(2) Effect As mentioned above, when multiple types of β phases with different properties are mixed in the surface layer, the sliding characteristics of the surface layer are significantly improved compared to those with a single β phase. Therefore, the surface layer exhibits excellent durability even at high speeds and under high surface pressure, and the strength of the surface layer is also significantly improved.
（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１
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 1 as a titanium alloy structural member.
The rocker arm 1 shown in FIG.
has.
ロッカアームｌの製造に当っては、Ｔｉ−６Ａｆｆｉ−
４Ｖのｍ戒を有する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は素材に改質処理
を施すことによって形成されたものである。When manufacturing rocker arm l, Ti-6Affi-
An α+β type titanium alloy material having an m precept of 4V is used, and the surface layer 3 forming the slipper surface 2 is formed by subjecting the material to a modification treatment.
表層部３の金属＆ｌｌ織は、特性を異にする複数種、本
実施例では二種のβ相を混在させた組織である。The metal ≪ weave of the surface layer portion 3 is a structure in which a plurality of types, in this example, two types of β phases having different characteristics are mixed.
第２図に示す金属組織の概略図から明らかなように、第
１のβ相ｂ１は散点状に分布しており、また第２のβ相
ｂ２は、それら第１のβ相す、を囲繞して網状に展開し
ている。また表層部３は、均一に分散する硬質粒子ｐを
含有する。As is clear from the schematic diagram of the metallographic structure shown in FIG. 2, the first β phase b1 is distributed in a scattered manner, and the second β phase b2 is separated from the first β phases. It surrounds and develops into a net. Further, the surface layer portion 3 contains uniformly dispersed hard particles p.
改質処理に当って、Ｍｏ、Ｃ粉末およびＦｅ粉末を用い
て、高密度エネルギビームによる局所溶融合金化処理を
適用する関係から、第１のβ相ｂ１は、Ｍｏを１０重量
％以上含有するＭｏ９度の高いβ相であり、また第２の
β相すつはＦｅを３゜５重量％以上、１５重量％以下含
有するＦｅ濃度の高いβ相である。In the modification treatment, the first β phase b1 contains 10% by weight or more of Mo because the local melting alloying treatment using a high-density energy beam is applied using Mo, C powder, and Fe powder. It is a β phase with a high Mo9 degree, and the second β phase is a β phase with a high Fe concentration, containing Fe in an amount of 3.5% by weight or more and 15% by weight or less.
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
１０重量％以上含有させることによって、第１のβ相す
、を室温まで持ちきたすことができる。またＭｏは第１
のβ相ｂｌの摺動特性および耐熱性を向上させる効果を
有する。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 10% by weight or more, the first β phase can be brought to room temperature. Also, Mo is the first
This has the effect of improving the sliding properties and heat resistance of the β phase BL.
たりし、ＭＯの単独添加では、第１のβ相す。However, when MO is added alone, the first β phase is formed.
の硬さが低く、耐摩耗性が低下する６
Ｆｅは共析型β安定化元素である。Ｆｅを３．５重量％
以上含有させることによって、第２のβ相ｂ２の安定化
が図られ、また析出硬化作用を生じさせて第２のβ相ｂ
２の硬さおよび強度を向上させることができる。6Fe, which has low hardness and reduces wear resistance, is a eutectoid β-stabilizing element. 3.5% by weight of Fe
By containing the above, the second β phase b2 is stabilized, and a precipitation hardening effect is caused to form the second β phase b2.
The hardness and strength of No. 2 can be improved.
た＼°し、Ｆｅの含有量が１５重量％を上回ると、Ｆｅ
の固溶性が低いことに起因して、偏析等を生じ、安定し
た第２のβ相ｂ２が得られなくなり、強度も低下する。However, if the Fe content exceeds 15% by weight, Fe
Due to the low solid solubility, segregation etc. occur, making it impossible to obtain a stable second β phase b2, and the strength also decreases.
したがって、Ｆｅ含有量の上限は１５重量％に設定され
る。Therefore, the upper limit of the Fe content is set at 15% 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第２のβ
相ｂ２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 when only Fe is added without adding Mo, an intermetallic compound is formed due to the precipitation hardening effect, and the second β
Although phase b2 tends to become brittle, this problem can be solved by using MO in combination.
第３図は、母材（Ｔ １−６Ａｊ２−４ Ｖ）と、その
母材に２６重量％ＭＯを含有させた比較表層部と、母材
に２６重量％Ｍｏおよび８重量％Ｆｅを含有させた本発
明表層部の硬さを比較したものである。Figure 3 shows a base material (T 1-6Aj2-4 V), a comparative surface layer part in which the base material contains 26% by weight of MO, and a comparative surface layer in which the base material contains 26% by weight of Mo and 8% by weight of Fe. The hardness of the surface layer portion of the present invention is compared.
第３図より、ＭＯのみ含有する比較表層部は、母材に比
べて硬さの上昇程度が極めて少ないが、Ｆｅを含有させ
ると、硬さが大幅に上昇することが判る。From FIG. 3, it can be seen that the comparative surface layer containing only MO shows a very small increase in hardness compared to the base material, but when Fe is added, the hardness increases significantly.
表層は、各種表層部の平均組成（推定）、平均硬さ、Ｍ
ｏ、Ｃ粉末とＦｅＣ粉末供給比率を示し、第４図は表層
に基づくグラフを示す。The average composition (estimated), average hardness, and M of the surface layer are as follows:
o, C powder and FeC powder supply ratio, and FIG. 4 shows a graph based on the surface layer.
表 Ｉ
表層部Ｎα■、■が本発明に該当し、その外は比較例で
ある。Table I The surface layer parts Nα■ and ■ correspond to the present invention, and the rest are comparative examples.
表１および第４図より、Ｆｅの含有量は３．５〜１５重
量％、好ましくは５重量％以上であることが判る。From Table 1 and FIG. 4, it can be seen that the Fe content is 3.5 to 15% by weight, preferably 5% by weight or more.
第２のβ相す、における網目４の直径は、摺動特性およ
び強度向上の観点から、１０μｍ以下といった微細であ
ることが望ましい。The diameter of the mesh 4 in the second β phase is preferably as fine as 10 μm or less from the viewpoint of improving sliding properties and strength.
硬質粒子Ｐは、改質処理におけるＭｏ、Ｃ→２Ｍｏ十Ｃ
５Ｔｉ＋Ｃ−＋ＴｉＣの反応により析出した炭化物、即
ち、Ｔｉｃ粒子であり、その硬質粒子ｐの体積分率（Ｖ
ｆ）は、１０％以上、３０％以下に設定される。この硬
質粒子ｐの含有により、表層部３の硬さを確保して、そ
の耐摩耗性を向上させることができる。即ち、前記第１
．第２のβ相す、、ｂ、および硬質粒子Ｐよりなる表層
部３は、高速、且つ高面圧摺動条件下において、従来の
鉄系焼結摺動部材と同等若しくはそれ以上の耐摩耗性を
発揮する。The hard particles P are Mo, C→2Mo+C in the modification treatment.
The carbide precipitated by the reaction of 5Ti+C-+TiC is Tic particles, and the volume fraction of the hard particles p (V
f) is set to 10% or more and 30% or less. By containing the hard particles p, the hardness of the surface layer portion 3 can be ensured and its wear resistance can be improved. That is, the first
．． The surface layer 3 made of the second β phase S, b, and hard particles P has wear resistance equal to or higher than that of conventional iron-based sintered sliding members under high speed and high surface pressure sliding conditions. Demonstrate your sexuality.
また、硬質粒子ｐは析出現象により生じるものであるか
ら、１〜５μｍの粒径を有する微細粒子であり、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 the hard particles p are generated by a precipitation phenomenon, they are fine particles with a particle size of 1 to 5 μm and have good dispersibility. Furthermore, since the particle shape is round, the amount of wear on the sliding partner material is small. It has the advantage of being less aggressive, such as increasing
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 particle size, but the crushed powder has an angular shape and exerts an abrasive effect, so it attacks the sliding material. In order to obtain particles with high properties and small particle diameters within the above range, precision classification processing must be performed, resulting in a huge increase in cost.
なお、硬質粒子ｐ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、また表要部３が脆化し、さ
らに硬質粒子ｐが脱落し易くなる。It should be noted that if the volume fraction of the hard particles p is less than 10%, the above effect cannot be obtained, while if it exceeds 30%, the aggressiveness towards the sliding mating material increases, and the surface part 3 becomes It becomes brittle, and the hard particles p become more likely to fall off.
第５図は、表層部３における硬質粒子ｐの体積分率（Ｖ
ｆ）とビッカース硬さ（最高硬さ）との関係を示す。FIG. 5 shows the volume fraction (V
The relationship between f) and Vickers hardness (maximum hardness) is shown.
この場合、母材としては前記同様のα十β型チタン合金
が用いられ、Ｍｏｚ Ｃ粉末の添加量を変化させてＴｉ
Ｃ粒子の析出量を調節したものである。In this case, the same α-decade-β type titanium alloy as described above is used as the base material, and the amount of Moz C powder added is changed to
The amount of C particles precipitated was adjusted.
第５図より硬質粒子ｐの体積分率の増加に伴い表層部３
の硬さが上昇することが判る。From FIG. 5, as the volume fraction of hard particles p increases, the surface layer 3
It can be seen that the hardness increases.
以下、ロッカアーム１の改質処理について説明する。The modification process for the rocker arm 1 will be described below.
第６図は改質処理法を示し、前記母材（Ｔｊ −６ＡＩ
２−４Ｖ）よりなるロッカアーム用素材１０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より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Ｍ。Figure 6 shows the modification treatment method, in which the base material (Tj -6AI
2-4V) is moved in the direction of the arrow, the 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 shielding gas, is supplied from the gas supply nozzle 6. M from powder supply nozzle 7.
２Ｃ粉末およびＦｅ粉末をそれぞれ供給するものである
。It supplies 2C powder and Fe powder respectively.
改質処理条件は次の通りである。The modification treatment conditions are as follows.
ロッカアーム用素材１゜の移動速度（処理速度） ：
３００ ｍ／ｗｉｎ
炭酸ガスレーザ：出力 ５ｋＷ、スポット径２ｍ＋、振
幅 ５肛、パワー密度５〜６Ｘ１０’Ｗ／ｃｄ
ＭｏｚＣ粉末：直径 １０〜４４μｍ、供給量１５、７
ｇ／＋ａｉｎ ； Ｆ Ｃ粉末：純度 ９９％以上
、粒度 ２００メツシユ以下、供給量 ４．６ｇ／鰯ｉ
ｎ
表皮層３の形成は、次の第１〜第４過程を経て行われる
。Movement speed of rocker arm material 1° (processing speed):
300 m/win Carbon dioxide laser: Output 5kW, spot diameter 2m+, amplitude 5 anus, power density 5~6X10'W/cd MozC powder: diameter 10~44μm, supply amount 15,7
g/+ain; FC powder: purity 99% or more, particle size 200 mesh or less, supply amount 4.6 g/sardine i
n The formation of the epidermis layer 3 is performed through the following first to fourth steps.
第１過程７３２００℃以上の腐度域で母材、ＭＯＺＣ粉
末およびＦｅ粉末が溶解する。その際、Ｍｏｚ Ｃ→２
Ｍｏ十Ｃの反応が生じる。In the first step, the base material, MOZC powder, and Fe powder are dissolved in the rottenness range of 73,200°C or higher. At that time, Moz C → 2
A Mo-C reaction occurs.
第２過程：３２００°Ｃ以下の温度域で、Ｔｉ十Ｃ−Ｔ
ｉＣの反応が生じて、硬質粒子としてのＴｉＣ粒子が析
出する。2nd process: In the temperature range below 3200°C, Ti
An iC reaction occurs and TiC particles as hard particles are precipitated.
第３過程：約２０００ ’Ｃの温度域で、Ｍｏｚ度の高
い第１のβ相す、が晶出を開始する。Third step: In a temperature range of about 2000'C, the first β phase with a high Moz degree starts to crystallize.
第４過程：約１４００°Ｃの温度域で、Ｆｅ濃度の高い
第２のβ相ｂ２が晶出を開始する。Fourth step: In a temperature range of about 1400°C, the second β phase b2 with a high Fe concentration starts to crystallize.
第７図は前記改質処理により得られた表層部３のＸマイ
クロアナライザ（ＥＰＭＡ）による金属組織を示す顕微
鏡写真である。FIG. 7 is a micrograph showing the metal structure of the surface layer 3 obtained by the above-mentioned modification treatment, taken using an X-micro analyzer (EPMA).
第７図（ａ）はＭｏの分布状況を示し、白色部分がＭＯ
であって、Ｍｏ濃度の高い第１のβ相ｂ１が散点状に分
布していることが判る。Figure 7(a) shows the distribution of Mo, and the white part is MO.
It can be seen that the first β phase b1 with a high Mo concentration is distributed in a dotted manner.
第７図〜）はＦｅの分布状況を示し、白色部分がＦｅで
あって、Ｆｅ濃度の高い第２のβ相ｂ２が黒色のＭｏ１
度の高い第１のβ相す、を囲繞して網状に展開している
ことが判る。Figure 7~) shows the distribution of Fe, where the white part is Fe and the second β phase b2 with a high Fe concentration is the black Mo1.
It can be seen that the first β phase, which has a high degree of strength, is surrounded by a net-like structure.
第１のβ相ｂ１と第２のβ相ｂ２による網目構造は、再
凝固過程における両相ｂ＋、ｂｚの凝固点の差により生
じるものであり、凝固点の高い第１のβ相ｂ１が先に晶
出し、その間隙を第２のβ相す、が埋めることによって
形成される。The network structure formed by the first β phase b1 and the second β phase b2 is caused by the difference in the freezing point of both phases b+ and bz during the resolidification process, and the first β phase b1, which has a higher freezing point, crystallizes first. The second β phase is formed by filling the gap with the second β phase.
炭酸ガスレーザといった高密度エネルギビームによる局
所溶融合金化処理においては、溶融径自己冷却による急
速凝固作用が得られるので、網目構造が微細で、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 beam such as a carbon dioxide laser, rapid solidification is achieved by self-cooling of the melt diameter, resulting in a fine and homogeneous network 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、Ｍｏｗ 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 for using a carbide such as Mow C 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 carbide, 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！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。In other words, metal Mo is a high melting point material with a melting point of 2610°C, and until then it is difficult to alloy with Ti in a titanium alloy with a melting point of 1668°C. However, when used in the form of a carbide, its melting point is Since the temperature decreases to about 2400°C, the difference in melting point with Ti becomes smaller and alloying becomes easier.
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
。Further, carbide powder has a higher endothermic ability (light absorption ability) than metal Mo, and is therefore advantageous in terms of energy efficiency.
前記改質処理により得られた表層部３の平均組成は、Ｔ
ｉ−２６Ｍｏ−１１，８Ｆｅ−４，ＩＡ／！−３，２ｖ
であり、ＴｉＣ粒子の平均粒径は２．４ａｍ。The average composition of the surface layer 3 obtained by the modification treatment is T
i-26Mo-11,8Fe-4,IA/! -3,2v
The average particle size of the TiC particles is 2.4 am.
体積分率は１８．７５％であった。The volume fraction was 18.75%.
この場合、第１のβ相す、におけるＭｏの含有量は４０
．５重量％で、またＦｅの含有量は５．７重量％であり
、したがって第１のβ相す、ではＭ。In this case, the Mo content in the first β phase is 40
．． 5% by weight, and the content of Fe is 5.7% by weight, so the first β phase is M.
の濃度が高い、一方、第２のβ相ｂ２におけるＦｅの含
有量は２２．４重量％で、またＭｏの含有量は１０．０
重量％であり、したがって第２のβ相ｂｔではＦｅの濃
度が高い。On the other hand, the content of Fe in the second β phase b2 is 22.4% by weight, and the content of Mo is 10.0% by weight.
% by weight, and therefore the second β phase bt has a high concentration of Fe.
第８図は前記表層部３の深さと硬さとの関係を示す。図
中、ＳＩは改質処理前のスリッパ面位置を、またＳ２は
改質処理後のスリッパ面位置をそれぞれ示し、改質処理
により厚さが若干増加する。FIG. 8 shows the relationship between the depth and hardness of the surface layer 3. In the figure, SI indicates the slipper surface position before the modification treatment, and S2 indicates the slipper surface position after the modification treatment, and the thickness increases slightly due to the modification treatment.
第８図より、改質処理によってスリッパ面２の硬さ（Ｈ
ｖ）は約７５０といった高い値を示すことが判る。From FIG. 8, the hardness (H
It can be seen that v) exhibits a high value of about 750.
第９図は、本発明における表層部３と、スリッパ面２を
構成する各種チップ材の摺動試験結果を示す０表層は、
第９図における各種テストピースＡ−Ｆの材質を示す。FIG. 9 shows the sliding test results of the surface layer 3 and various chip materials constituting the slipper surface 2 in the present invention.
The materials of various test pieces A to F in FIG. 9 are shown.
表 ■
摺動試験はチップオンディスク式摺動試験に基づいて行
われ、試験条件は、ディスクの材質：構造用鋼（ＪＩＳ
ＳＣＭ ４２０Ｈ）、浸炭処理；摺動速度： ７
．５ ｍ ／ｓｅｃ ；荷重：Ｏ〜３００ｋｇｆまでｌ
ｏｋｇ／ｗｉｎで上昇；潤滑油：昭和’／エル石油社製
、（商品名１０Ｗ−３０、ウルトラＵ）；潤滑油供給量
： １１ ｃ ｃ／ｗｉｎ （室温）、である。Table ■ The sliding test was conducted based on the chip-on-disc sliding test, and the test conditions were as follows: Disk material: structural steel (JIS
SCM 420H), carburizing treatment; sliding speed: 7
．． 5 m/sec; Load: 0 to 300 kgf
lubricating oil: manufactured by Showa'/L Oil Co., Ltd. (trade name 10W-30, Ultra U); lubricating oil supply amount: 11 cc/win (room temperature).
限界焼付荷重は、前記荷重上昇に伴い、テストピースが
焼付きを生じときの荷重を求めた。The limit seizure load was determined by the load at which the test piece caused seizure as the load increased.
第９図から明らかなように、本発明においては限界焼付
荷重が３００ｋｇｆ以上であり、これは従来の高Ｃｒ鉄
系焼結材に相当する。As is clear from FIG. 9, in the present invention, the critical seizure load is 300 kgf or more, which corresponds to the conventional high Cr iron-based sintered material.
なお、本発明はチタン製構造部材にも通用される。Note that the present invention is also applicable to titanium structural members.
Ｃ０発明の効果
本発明によれば、表層部の金属Ｍｉ織を前記のように特
定することによって、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。C0 Effects of the Invention According to the present invention, by specifying the metallic Mi weave in the surface layer as described above, a titanium or titanium alloy structural member is provided which has a surface layer with excellent sliding properties and strength. be able to.
第１図はロッカアームの要部破断正面図、第２図は表層
部の金属組織を示す概略図、第３図は表層部等のビッカ
ース硬さを示すグラフ、第４図は表層部におけるＦｅ含
有量と平均ビッカース硬さとの関係を示すグラフ、第５
図は表層部における硬質粒子の体積分率とピンカース硬
さとの関係を示すグラフ、第６図は改質処理法の説明図
、第７図は表層部の金属組織を示す顕微鏡写真、第８図
は表層部の深さとピンカース硬さとの関係を示すグラフ
、第９図は表層部等の限界焼付荷重を示すグラフである
。
ｂ、、ｂ、・・・第１．第２のβ相、ｐ・・・硬質粒子
、１・・・ロッカアーム（構造部材）、３・・・表層部
、４・・・綱目
特許
出
願人
本田技研工業株式会社Figure 1 is a cutaway front view of the main part of the rocker arm, Figure 2 is a schematic diagram showing the metallographic structure of the surface layer, Figure 3 is a graph showing the Vickers hardness of the surface layer, etc., and Figure 4 is the Fe content in the surface layer. Graph showing the relationship between quantity and average Vickers hardness, No. 5
The figure is a graph showing the relationship between the volume fraction of hard particles in the surface layer and Pinkers hardness, Figure 6 is an explanatory diagram of the modification treatment method, Figure 7 is a micrograph showing the metal structure of the surface layer, and Figure 8 9 is a graph showing the relationship between the depth of the surface layer and Pinkers hardness, and FIG. 9 is a graph showing the limit seizure load of the surface layer, etc. b,,b,... 1st. Second β phase, p...Hard particles, 1...Rocker arm (structural member), 3...Surface layer portion, 4...Line patent applicant Honda Motor Co., Ltd.
Claims (5)
相を混在させた組織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) Multiple types of β with different metal structures in the surface layer
A structural member made of titanium or a titanium alloy, characterized by a structure containing a mixture of phases.
それら第１のβ相を囲繞して網状に展開する第２のβ相
とよりなる、第（１）項記載のチタンまたはチタン合金
製構造部材。(2) the metal structure includes a first β phase distributed in a dotted manner;
The titanium or titanium alloy structural member according to item (1), comprising a second β phase that surrounds the first β phase and develops in a net shape.
下である、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 or titanium alloy structural member according to item (2), wherein the diameter of the mesh in the second β phase is 10 μm or less.
また前記第２のβ相はＦｅを３．５重量％以上、１５重
量％以下含有している、第（２）または第（３）項記載
のチタンまたはチタン合金製構造部材。(4) the first β phase contains Mo at 10% by weight or more,
The titanium or titanium alloy structural member according to item (2) or item (3), wherein the second β phase contains Fe in an amount of 3.5% by weight or more and 15% by weight or less.
、その硬質粒子の体積分率（Ｖｆ）は、１０％以上、３
０％以下である、第（１），第（２），第（３）または
第（４）項記載のチタンまたはチタン合金製構造部材。(5) The surface layer portion contains uniformly dispersed hard particles, and the volume fraction (Vf) of the hard particles is 10% or more, 3
0% or less, the titanium or titanium alloy structural member according to item (1), item (2), item (3), or item (4).
Priority Applications (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1204287A JPH0699821B2 (en) | 1989-08-07 | 1989-08-07 | Structural member made of titanium or titanium-based alloy |
| US07/563,660 US5139585A (en) | 1989-08-07 | 1990-08-07 | Structural member made of titanium alloy having embedded beta phase of different densities and hard metals |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1204287A JPH0699821B2 (en) | 1989-08-07 | 1989-08-07 | Structural member made of titanium or titanium-based alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0368786A true JPH0368786A (en) | 1991-03-25 |
| JPH0699821B2 JPH0699821B2 (en) | 1994-12-07 |
Family
ID=16487981
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1204287A Expired - Fee Related JPH0699821B2 (en) | 1989-08-07 | 1989-08-07 | Structural member made of titanium or titanium-based alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0699821B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103628056A (en) * | 2013-12-09 | 2014-03-12 | 山东建筑大学 | Material for TA15 titanium alloy surface laser cladding and laser cladding method |
-
1989
- 1989-08-07 JP JP1204287A patent/JPH0699821B2/en not_active Expired - Fee Related
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103628056A (en) * | 2013-12-09 | 2014-03-12 | 山东建筑大学 | Material for TA15 titanium alloy surface laser cladding and laser cladding method |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0699821B2 (en) | 1994-12-07 |
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