JPS6342357A - Wear-resistant ferrous sintered alloy - Google Patents
Wear-resistant ferrous sintered alloyInfo
- Publication number
- JPS6342357A JPS6342357A JP18747186A JP18747186A JPS6342357A JP S6342357 A JPS6342357 A JP S6342357A JP 18747186 A JP18747186 A JP 18747186A JP 18747186 A JP18747186 A JP 18747186A JP S6342357 A JPS6342357 A JP S6342357A
- Authority
- JP
- Japan
- Prior art keywords
- wear
- powder
- carbides
- borides
- matrix
- 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
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 42
- 239000000956 alloy Substances 0.000 title claims abstract description 42
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 title abstract 3
- 239000011159 matrix material Substances 0.000 claims abstract description 22
- 150000001247 metal acetylides Chemical class 0.000 claims abstract description 21
- 239000002244 precipitate Substances 0.000 claims abstract description 18
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 14
- 229910052796 boron Inorganic materials 0.000 claims abstract description 12
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 11
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 9
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 6
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 6
- 239000000203 mixture Substances 0.000 claims abstract description 6
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 33
- 229910052742 iron Inorganic materials 0.000 claims description 19
- 229910052721 tungsten Inorganic materials 0.000 claims description 16
- 238000001556 precipitation Methods 0.000 claims description 6
- 239000012535 impurity Substances 0.000 claims description 3
- 239000000843 powder Substances 0.000 abstract description 28
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 abstract description 5
- 239000002184 metal Substances 0.000 abstract description 5
- 229910052751 metal Inorganic materials 0.000 abstract description 5
- 229910017116 Fe—Mo Inorganic materials 0.000 abstract description 3
- 229910018540 Si C Inorganic materials 0.000 abstract description 2
- 239000002994 raw material Substances 0.000 abstract description 2
- 229910010271 silicon carbide Inorganic materials 0.000 abstract description 2
- 150000002739 metals Chemical class 0.000 abstract 2
- 239000000463 material Substances 0.000 description 19
- 230000013011 mating Effects 0.000 description 14
- 230000000694 effects Effects 0.000 description 12
- 230000007423 decrease Effects 0.000 description 10
- 239000002245 particle Substances 0.000 description 7
- 230000000052 comparative effect Effects 0.000 description 6
- 238000005245 sintering Methods 0.000 description 5
- 229910001018 Cast iron Inorganic materials 0.000 description 4
- 229910000521 B alloy Inorganic materials 0.000 description 3
- 238000005299 abrasion Methods 0.000 description 3
- 238000002485 combustion reaction Methods 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 239000007791 liquid phase Substances 0.000 description 3
- 238000007747 plating Methods 0.000 description 3
- 239000007921 spray Substances 0.000 description 3
- 238000000137 annealing Methods 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 238000000354 decomposition reaction Methods 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 239000011148 porous material Substances 0.000 description 2
- 229910017060 Fe Cr Inorganic materials 0.000 description 1
- 229910002544 Fe-Cr Inorganic materials 0.000 description 1
- 206010020772 Hypertension Diseases 0.000 description 1
- 229910001096 P alloy Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- UPHIPHFJVNKLMR-UHFFFAOYSA-N chromium iron Chemical compound [Cr].[Fe] UPHIPHFJVNKLMR-UHFFFAOYSA-N 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 229910052735 hafnium Inorganic materials 0.000 description 1
- 239000000314 lubricant Substances 0.000 description 1
- 238000001000 micrograph Methods 0.000 description 1
- 239000011812 mixed powder Substances 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 239000012071 phase Substances 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 235000020083 shōchū Nutrition 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 230000003746 surface roughness Effects 0.000 description 1
- 238000004381 surface treatment Methods 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
- 239000011701 zinc Substances 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【発明の詳細な説明】
［発明の目的］
（産業上の利用分野）
本発明は、耐摩耗性が要求される部品の素材として利用
され、例えば内燃機関のロッカアームやタペット等の高
圧面のかかる摺動部に使用した場合にすぐれた＃摩耗性
となじみ性を発揮する鉄基焼結合金に関するものである
。Detailed Description of the Invention [Objective of the Invention] (Industrial Field of Application) The present invention can be used as a material for parts that require wear resistance, such as rocker arms and tappets of internal combustion engines that are subject to high pressure. This relates to an iron-based sintered alloy that exhibits excellent wear resistance and conformability when used in sliding parts.
（従来の技術）
近年、内燃機関に対する高速化および高出力化などの要
求に伴って内燃機関の動弁系部材の摩耗が問題となりつ
つあり、特にロッカアームやタペットのカムシャフトと
の摺動部に対する耐久性の要求はきわめて厳しいものと
なっている。(Prior Art) In recent years, with the demand for higher speeds and higher outputs for internal combustion engines, wear and tear on the valve train members of internal combustion engines has become a problem, especially on the sliding parts of the rocker arm and tappet with the camshaft. Durability requirements are extremely strict.
一〇Ｑに、ロッカアームやタペットのカムシャフトとの
摺動部は高い面圧を受けるものであるため、すぐれた耐
摩耗性、；耐スカッフィング性および１耐ピツチング性
を兼ね備えかつカムシャフトとのなじみ性をも合わせ持
つことが要求される。10 Q. Since the sliding parts of the rocker arm and tappet with the camshaft are subject to high surface pressure, it has excellent wear resistance, scuffing resistance, pitting resistance, and compatibility with the camshaft. It is required to have both gender.
従来、ロッカアームにはチル鋳鉄製のもの、ロッカアー
ム摺動部にＣｒめっきや自溶性合金の溶射肉盛などの表
面処理を施したもの（例えば、新編 自動車工学便覧
第１２編 第１−５４頁〜第１−５５頁）、あるいは鉄
−Ｃｒ−Ｃ系の高合金粉末の圧粉体を液相焼結したもの
（ｍえば、特開昭５７−１０８２４６号）などが使用さ
れている。Conventionally, rocker arms have been made of chilled cast iron, and rocker arm sliding parts have been subjected to surface treatments such as Cr plating or thermal spray overlay of self-fluxing alloys (for example, new Automotive Engineering Handbook).
Volume 12, pages 1-54 to 1-55), or liquid-phase sintered compacts of iron-Cr-C high alloy powders (e.g., JP-A-57-108246) etc. are used.
（発明が解決しようとする問題点）
しかしながら、上記のうち、チル鋳鉄製のロッカアーム
は耐ピツチング性や耐摩耗性の点で問題があり、Ｃｒめ
っきを施したロッカアームではめっき層の′ＡＩＩＩ＆
の問題があり、溶射肉盛を施したロッカアームではスカ
ッフィングや相手部材のカムシャフトに対する摩耗など
の問題がある。また、鉄−Ｃｒ−Ｃ系焼結合金製のロッ
カアームの場合は前記チル鋳物、Ｃｒめっき、溶射肉盛
製のロッカアームにくらべるとかなり良好な特性を示す
ことが多いが、面圧が非常に高くなる場合等には自分自
身の耐摩耗性が十分でないばかりでなく、カムシャフト
の摩耗量も大きくなってしまい、要求特性を満足するも
のになっていないのが現状である。(Problems to be Solved by the Invention) However, among the above, the rocker arm made of chilled cast iron has problems in terms of pitting resistance and wear resistance, and the rocker arm coated with Cr has the plating layer 'AIII &
Rocker arms with thermal spray overlays have problems such as scuffing and wear on the camshaft of the mating member. In addition, rocker arms made of iron-Cr-C sintered alloys often exhibit considerably better properties than rocker arms made of chill casting, Cr plating, or thermal spray overlay, but the surface pressure is extremely high. In such cases, not only the wear resistance of the camshaft itself is insufficient, but also the amount of wear on the camshaft increases, and the current situation is that the required characteristics are not satisfied.
そこで本発明者等は、上記のような観点から、すぐれた
耐摩耗性、耐スカッフィング性および耐ピツチング性を
持つだけでなく、相手部材とのなじみ性をも合わせ持つ
材料を開発することを目的として種々の研究を実施した
結果、本発明を完成した。Therefore, from the above viewpoint, the present inventors aimed to develop a material that not only has excellent wear resistance, scuffing resistance, and pitting resistance, but also has good compatibility with the mating member. As a result of conducting various researches, the present invention was completed.
［発明の構成］
（問題点を解決するための手段）
本発明による耐摩耗性鉄基焼結合金は、重着比で、ＭＯ
およびＷのいずれか１種または２種；５〜３０％、Ｃｒ
； １０％以下、Ｓｉ；０．１−０．９％、Ｍ ｎ ；
０ 、７％以下、Ｐ；０．０５％以下、Ｃ；０．１〜
２．０％、Ｂ、０．５〜２．０％、残部Ｆｅおよび不純
物からなる組成を有し、ベイナイトおよび／または焼も
どしマルテンサイトよりなるマトリックスに、粒径ＩＩ
Ｌｍ以上２０ｇｍ以下の微細な硼化物もしくは炭硼化物
と炭化物が共存していてこれらの硬質析出物が面積比で
１０％以上分散した組織を有することを特徴としている
。そして、このような組成および組織を有する鉄基焼結
合金がすぐれた摺動Ｉｌ耗性を示し、とくに例えばロッ
カアームのカム摺動部に使用した場合には極めて優れた
性能を発揮するという知見を得たものである。[Structure of the Invention] (Means for Solving the Problems) The wear-resistant iron-based sintered alloy according to the present invention has a weight ratio of MO
and any one or two of W; 5 to 30%, Cr
; 10% or less, Si; 0.1-0.9%, M n ;
0, 7% or less, P: 0.05% or less, C: 0.1~
2.0%, B, 0.5 to 2.0%, the balance is Fe and impurities, and the matrix is composed of bainite and/or tempered martensite, with grain size II
It is characterized by having a structure in which fine borides or carbides and carbides of Lm or more and 20 gm or less coexist, and these hard precipitates are dispersed in an area ratio of 10% or more. Furthermore, we discovered that an iron-based sintered alloy having such a composition and structure exhibits excellent sliding wear resistance, and exhibits extremely excellent performance, especially when used in the cam sliding part of a rocker arm, for example. That's what I got.
本発明は上記知見に基づいてなされたものであり、以下
に成分組成ならびに硬質析出物の粒径。The present invention has been made based on the above findings, and the component composition and particle size of the hard precipitate are described below.
種類および分布を上記の通りに限定した理由を説明する
。The reason for limiting the types and distribution as above will be explained.
く成分組成〉
ＭＯおよびＷ；
ＭｏおよびＷは成分中のＦｅやＣｒとともにＣやＢと結
合して複硼化物もしくは複炭砿化物と複炭化物を形成し
て耐摩耗性を午え、一部はマトリックス中に固溶して当
該マトリックスを強化するとともに焼戻し硬化能を高め
る作用があるが。Component composition> MO and W; Mo and W, along with Fe and Cr in the components, combine with C and B to form complex borides or complex carbides and complex carbides, which provide wear resistance, and some of them It acts as a solid solution in the matrix to strengthen the matrix and increase temper hardening ability.
５％未満では所望の効果が得られずに＃摩耗性不足とな
り、３０％を超えて含有させてもより一層の改善効果は
認められず、経済的でないことからその含有量を５〜３
０％と定めた。If it is less than 5%, the desired effect cannot be obtained and the abrasion properties are insufficient, and even if it is contained more than 30%, no further improvement effect is observed, and it is not economical, so the content is reduced to 5 to 3%.
It was set as 0%.
Ｃｒ；
ＣｒはＦｅ、Ｍｏ、Ｗ等とともに複硼化物もしくは復炭
硼化物と複炭化物を形成して＃摩耗性を向上させるとと
もに、マトリックス中に固溶して焼入性を増大させ、さ
らに焼戻し硬化能を高める効果を有するとともに基地の
耐食性を向上させる効果もあるので、ディーゼルエンジ
ン用のロッカアームチップ等に使用する場合には添加す
ることが必要であるが、摩耗条件が比較的楽なエンジン
用ロッカアームチップ等では無添加でもかまわない、そ
して、添加する場合に、１０％を超えて含有させてもよ
り一層の改善効果がないばかりでなく、機械的強度が低
下して相手材への攻撃性が増大してしまうことからその
含イ■量を１０％以下とすることが好ましい。Cr; Cr forms a complex boride or a complex carbide with a double carbide boride together with Fe, Mo, W, etc. to improve the wear resistance, and also solid-solves in the matrix to increase the hardenability and further tempering. It has the effect of increasing the hardening ability and also improves the corrosion resistance of the base, so it is necessary to add it when used in rocker arm tips for diesel engines, but it is used for engines with relatively easy wear conditions. For rocker arm chips, etc., no additives can be used, and if they are added, even if they are added in excess of 10%, not only will there be no further improvement effect, but the mechanical strength will decrease and the aggressiveness of the mating material will increase. It is preferable to keep the i content to 10% or less.
Ｓ ｉ ；
Ｓｔは０．１％未満の添加量では脱酸効果が少なく、粉
末中の酸素含有量が多くなって焼結性が低下するととも
にＭ２Ｃ系の粗大な板状炭化物が析出しやすくなり相手
部材とのなじみ性が低下する。一方、添加量が０．９％
を超えても脱酸効果の向上もなく、粉末が丸くなってし
まい成形性が低下するだけであることから、その含有量
を０．１〜０．９％と定めた。S i ; If the amount of St added is less than 0.1%, the deoxidizing effect will be small, the oxygen content in the powder will increase, the sinterability will decrease, and M2C-based coarse plate-like carbides will easily precipitate. Compatibility with the mating member decreases. On the other hand, the amount added is 0.9%
If the content exceeds 0.1%, the deoxidizing effect will not be improved and the powder will become rounded and the moldability will be reduced. Therefore, the content was set at 0.1% to 0.9%.
Ｍｎ；
Ｍｎは前述したＳｉと同じように脱酸効果があり、添加
することによって粉末中の酸素含有量を下げて焼結性を
向上させるが、０．７％を超えると粉末の形状が丸くな
って粉末の成形性が低下してしまうので、その含有量を
０．７％以下と定めた。Mn: Like the aforementioned Si, Mn has a deoxidizing effect, and adding it lowers the oxygen content in the powder and improves sinterability, but if it exceeds 0.7%, the shape of the powder becomes round. Therefore, the content was set at 0.7% or less.
Ｐ；
Ｐは耐摩耗性焼結合金の場合において焼結促進元素とし
て一般に０．２〜０．８９６程度添加する手法が広く用
いられているが、本発明による焼結合金の場合はＰの添
加量が０．０５％を超えた場合に、複硼化物あるいは復
炭硼化物が粗大化して相手材とのなじみ性が低下すると
ともに１粒界に複硼化物あるいは復炭硼化物がネ−ｙ
トワーク状に析出して強度が低下してしまうことにより
、特に高面圧がかかった場合の耐ピッチング特性も低下
してしまうことからその含有量を０．０５％以下と定め
た。P: In the case of wear-resistant sintered alloys, P is generally added as a sintering promoting element in a range of about 0.2 to 0.896, but in the case of the sintered alloys of the present invention, P is added. If the amount exceeds 0.05%, the complex boride or carbon boride becomes coarse and the compatibility with the mating material decreases, and at the same time, the complex boride or the carbon boride becomes naive at one grain boundary.
The content was determined to be 0.05% or less because the steel precipitates in a network shape and reduces the strength, which also reduces the pitting resistance, especially when high surface pressure is applied.
Ｃ；
° Ｃはその一部がＭ ｏ 、 Ｗ 、 Ｃｒ 、 Ｖ
などの炭化物形成元素と結合して複炭化物を形成して耐
摩耗性を向上させ、残りはマトリックス中に固溶して高
い室温硬さと強度を与える作用を有するが、０．１％未
満ではその効果が認められず。C: Part of °C is Mo, W, Cr, V
It combines with carbide-forming elements such as to form double carbides and improves wear resistance, and the rest dissolves in the matrix and has the effect of providing high room temperature hardness and strength. However, if it is less than 0.1%, No effect was observed.
２．０％を超えると複炭化物の析出量増加と粗大化が起
こり、相手材とのなじみ性が低下することから、その含
有量を０．１〜２６０％と定めた。If it exceeds 2.0%, an increase in the amount of precipitated double carbides and coarsening will occur, resulting in a decrease in compatibility with the mating material, so the content is set at 0.1 to 260%.
このＣの添加方法としては、真空焼鈍を施したＦ ａ−
Ｍｏ −Ｗ−Ｃｒ−Ｓ ｉ −（Ｍｎ） −Ｃ系アトマ
イズ合金粉末の形で添加する必要゛がある。これはＣを
単独にグラファイト粉末の形で添加すると、後述するＢ
源として添加するＦｅ−ＢあるいはＦｅ−Ｃｒ−Ｂと結
びついて焼結時に粗大な炭硼化物を粒界に沿ってネット
ワーク状に析出させ相手材への攻撃性を増大してしまう
のに対して、真空焼鈍を施したＦｅ−Ｍｏ −Ｗ−Ｃｒ
−５ｉ −（Ｍｎ）−Ｃ系アトマイズ合金粉末の形で添
加した場合は、アトーｙイズ後の真空焼鈍時にＣは大部
分がＭ ｏ 、 Ｗ 、 Ｃｒ 、 Ｆ ｅ等と結びつ
いて微細な複炭化物としてアトマイズ合金粉末中に析出
することから、Ｆｅ−ＢやＦｅ−Ｃｒ−Ｂを添加しても
焼結時に粒界あるいは粒界に近い部分の複炭化物がＦｅ
−ＢやＦｅ−Ｃｒ−Ｂと結びついてもとの複炭化物より
は若干大きな復炭硼化物となるだけで、粒内の微細な複
炭化物は焼結後もそのまま残り、Ｆｅ−ＢやＦｅ−Ｃｒ
−Ｂとアトマイズ合金粉末中のＭｏおよびＷなどとの間
の分解・析出により生じた微細な複硼化物とともに均一
に分散した本発明による焼結合金特有の組織が得られる
ためである。As a method of adding C, Fa-
It is necessary to add it in the form of Mo-W-Cr-Si-(Mn)-C based atomized alloy powder. When C is added alone in the form of graphite powder, B
Coupled with Fe-B or Fe-Cr-B added as a source, coarse carborides are precipitated in a network shape along the grain boundaries during sintering, increasing the aggressiveness of the mating material. , Fe-Mo-W-Cr subjected to vacuum annealing
-5i When added in the form of -(Mn)-C-based atomized alloy powder, most of the C combines with Mo, W, Cr, Fe, etc. during vacuum annealing after atomization to form fine double carbides. Even if Fe-B or Fe-Cr-B is added, double carbides at the grain boundaries or near the grain boundaries will be precipitated in the atomized alloy powder as Fe-B.
-B and Fe-Cr-B combine to form a slightly larger double carbide than the original double carbide, and the fine double carbides within the grains remain as they are even after sintering, and Fe-B and Fe- Cr
This is because a unique structure of the sintered alloy according to the present invention is obtained, in which fine complex borides produced by decomposition and precipitation between -B and Mo, W, etc. in the atomized alloy powder are uniformly dispersed.
Ｂ；
Ｂは成分中のＭｏ、Ｗ、Ｃｒ、Ｆｅとともに複硼化物を
形成して耐摩耗性と耐なじみ性を与えるとともに、一部
はマトリックス中に固溶して焼入性を改９する。また、
上記複硼化物の一部はＣとも結びついて復炭硼化物を形
成して耐！？！耗性を向上させる。B; B forms a complex boride with Mo, W, Cr, and Fe in the components to provide wear resistance and conformability resistance, and a portion is dissolved in the matrix to improve hardenability. . Also,
A part of the above-mentioned complex boride also combines with C to form a carbonated boride and resists! ? ! Improve wear resistance.
このようにＢは微細な複硼化物あるいは復炭硼化物を形
成して本発明焼結合金の耐摩耗性と耐なじみ性を向上さ
せるのに必須の主要成分であるが、０．５％未満の添加
ではその効果が認められず、一方２．０％を超えてもよ
り一層の改善効果が認められずかえって複硼化物の粗大
化が起り。As described above, B is a major component essential for forming fine complex borides or carbonized borides to improve the wear resistance and conformability resistance of the sintered alloy of the present invention, but B is less than 0.5%. No effect was observed with the addition of 2.0%, while no further improvement was observed when the amount exceeded 2.0%, instead coarsening of the complex boride occurred.
相手材とのなじみ性が低下することからその含有量を０
．５〜２．０％と定めた。Since the compatibility with the mating material decreases, its content is reduced to 0.
．． It was set at 5 to 2.0%.
本発明による焼結合金のＢ添加量としては上述したよう
に０．５〜２．０％とする必要があるが、特に優れた特
性を示すのはＢ添加量がＭ ｏ ＋Ｗ添加量との間で、
［Ｍｏ＋Ｗ含有量（原子呈）］ ／ ＥＢ含有量（原子
量）コ＝０．８〜１．５の関係を満たしているときであ
る。これは上記原子比が１．５を超える場合は、複硼化
物の生成量が少なく本発明合金の特徴であるなじみ性が
低下してしまい、また前記原子比が０．８未満では複硼
化物が粗大化するとともにネットワーク状に粒界に析出
してしまい、相手材とのなじみ性が低下すると同時に自
分自身の耐ピツチング性が低下してしまうためである。As mentioned above, the amount of B added in the sintered alloy according to the present invention needs to be 0.5 to 2.0%, but particularly excellent properties are shown when the amount of B added is equal to the amount of M o + W added. Between,
This is when the relationship of [Mo+W content (atomic weight)]/EB content (atomic weight) = 0.8 to 1.5 is satisfied. This is because when the above atomic ratio exceeds 1.5, the amount of complex boride produced is small and the compatibility, which is a characteristic of the alloy of the present invention, is reduced, and when the above atomic ratio is less than 0.8, complex boride is formed. This is because the particles become coarser and precipitate at the grain boundaries in the form of a network, resulting in a decrease in compatibility with the mating material and at the same time a decrease in pitting resistance of itself.
このＢの添加方法としてはＦｅ−ＢあるいはＦｅ−Ｃｒ
−Ｂ系合金粉末の形で添加することが好ましい。The method of adding B is Fe-B or Fe-Cr.
It is preferable to add it in the form of -B alloy powder.
以上述べてきた成分のほか、硼化物形成元素であるＴｉ
、Ｚｒ、Ｈｆ、Ｃｏ等を必要に応じて１２％以下添加し
ても良い。特にＣｏはＭｏ、Ｗなどの一部と置換して複
硼化物を形成するだけでなく、マトリックス中に固溶し
て赤熱かたさを向−１ニさせるため、熱間での耐摩耗性
が要求される場合には添加することが特に効果的である
。In addition to the components mentioned above, Ti, which is a boride-forming element,
, Zr, Hf, Co, etc. may be added in an amount of 12% or less as necessary. In particular, Co not only replaces a part of Mo, W, etc. to form a complex boride, but also dissolves in the matrix and improves red-hot hardness, so it requires hot wear resistance. It is particularly effective to add it when
また、マトリックスがオーステナイト化しない範囲でＮ
ｉを添加しても良い、これはＮｉを添加するとマトリッ
クスの耐食性が向ｌ二するため、ディーゼルエンジンの
ＥＧＲ仕様のロッカアームや油圧リフタのように腐食摩
耗が厳しい部品への適用には特に効果がある。しかし、
Ｎｉの添加量、が多くなってマトリックスがオーステナ
イト化してしまった場合には、硬さが低下するだけでな
く、相手材との凝着性が大きくなってしまうため好まし
くない。In addition, as long as the matrix does not become austenite, N
It is also possible to add Ni, as the addition of Ni improves the corrosion resistance of the matrix, so it is particularly effective when applied to parts that are subject to severe corrosion and wear, such as rocker arms and hydraulic lifters for EGR specifications of diesel engines. be. but,
If the amount of Ni added increases and the matrix becomes austenitic, this is not preferable because not only the hardness decreases but also the adhesion with the mating material increases.
本発明による焼結合金の硬さとしては、ＨＲＣ５０〜６
５の範囲が好ましい、これは、ＨＲＣ５０未満では＃摩
耗性が不足し、ＨＲＣ６５を超えると相手材とのなじみ
性が低下するためである。したがって、マトリ−２クス
としては、ベイナイトおよび／または焼もどしマルテン
サイトを主体とするものとなすのがよい。The hardness of the sintered alloy according to the present invention is HRC50 to 6.
A range of 5 is preferable, because if the HRC is less than 50, the abrasion resistance is insufficient, and if the HRC is more than 65, the compatibility with the mating material decreases. Therefore, it is preferable that the matrix is mainly composed of bainite and/or tempered martensite.
また、本発明による焼結合金の理論密度比としては９０
％以上とすることが好ましい。これは、９０％未満の理
論密度比ではマトリックスの強度が低く、かつ空孔も大
きく、しかもこの空孔のもつ切欠作用によってマトリッ
クスが破壊されやすくなってピッチング摩耗が生じやす
くなるためである。Furthermore, the theoretical density ratio of the sintered alloy according to the present invention is 90
% or more is preferable. This is because when the theoretical density ratio is less than 90%, the strength of the matrix is low and the pores are large, and furthermore, the matrix is easily destroyed by the notch action of these pores, making it easy to cause pitting wear.
く硬質析出物の粒径〉
耐摩耗性焼結材料は一般に靭性および強度を有するマト
リックスに、硬質析出物を分散させることによって耐ス
カッフィング性と耐ピッチング性の向上を狙っている。Particle size of hard precipitates> Wear-resistant sintered materials generally aim to improve scuffing resistance and pitting resistance by dispersing hard precipitates in a matrix that has toughness and strength.
しかしながら、硬質析出物の粒径がｌｐｍ未満であると
摺動面の表面粗さよりも粒径が小さくなるために、硬質
相で荷重を分担して受ける効果が減少し、スカッフィン
グ摩耗が増加する。However, if the particle size of the hard precipitates is less than 1pm, the particle size will be smaller than the surface roughness of the sliding surface, so the effect of sharing the load with the hard phase will be reduced and scuffing wear will increase.
一方、硬質析出物の粒径が２０ｇｍを超えると、相手材
への攻撃性が大きくなるばかりでなく、脱落した場合に
はピッチング摩耗やアブレーシブ摩耗を引き起こしてし
まう。On the other hand, if the particle size of the hard precipitate exceeds 20 gm, not only will it be more aggressive towards the mating material, but if it falls off, it will cause pitting wear or abrasive wear.
そこで、本発明においては、粉末の状態で炭化物がすで
に析出した鉄基合金粉に、Ｆｅ−８合金粉もしくはＦｅ
−Ｃｒ−Ｂ合金粉を添加し、液相焼結させると同時に第
１表に示すような反応式に従う炭化物の分解、硼化物、
次回化物の析出といった非平衡反応を使うことによって
、粒径ｌμｍ以上２０ｐｍ以下の硬質析出物の分散状ｙ
Ｅを生み出すことに成功した。Therefore, in the present invention, Fe-8 alloy powder or Fe
-By adding Cr-B alloy powder and performing liquid phase sintering, at the same time decomposition of carbides according to the reaction formula shown in Table 1, boride,
By using non-equilibrium reactions such as precipitation of compounds, the dispersion shape of hard precipitates with a particle size of 1 μm or more and 20 pm or less can be improved.
succeeded in producing E.
そして、第１表に示すように、マトリックス中に分１敦
される硼化物は、主にＭ３ Ｂ２ （Ｍは、Ｆ ｅ
、 Ｍ ｏ 、 Ｗ 、 Ｃｒ ）からなるものとし、
炭化物は、主ｉ、ｍＭ６Ｃ（Ｍは、Ｆｅ、Ｍｏ、Ｗ）と
Ｍ７Ｃ３（Ｍは、Ｆｅ、Ｃｒ）からなるものとし、次回
化物は、Ｍ６Ｃ炭化物を析出サイトとして形成されたＭ
３ （Ｂ 、 Ｃ） ２ （Ｍは、Ｆｅ。As shown in Table 1, the boride added in the matrix is mainly M3 B2 (M is Fe
, M o , W , Cr ),
The carbide is mainly composed of M6C (M is Fe, Mo, W) and M7C3 (M is Fe, Cr), and the next carbide is M6C formed using the M6C carbide as a precipitation site.
3 (B, C) 2 (M is Fe.
Ｍｏ、Ｗ、Ｃｒ）からなるものとすることがより望まし
い、、。It is more desirable that the material be made of Mo, W, Cr).
く硼化物もしくは次回化物の析出状態〉一般に、粒界に
析出した炭化物は、マトリックスとの接合強度があまり
高くないために、摺切による繰返しの大きな剪断応力が
加わったときに炭化物の周囲に空孔が発生し、クラック
が進展していき、炭化物の脱落を伴ったピッチング摩耗
やアブレーシブ摩耗を生じやすい。Precipitation state of borides or borides〉Generally, carbides precipitated at grain boundaries do not have very high bonding strength with the matrix, so when repeated large shear stress due to abrasion is applied, voids form around the carbides. Holes are generated and cracks develop, which tends to cause pitting wear and abrasive wear accompanied by carbide drop-off.
そこで、本発明のより好ましい実施態様では、このよう
な欠点に鑑み、共有結合性を有するためにマトリックス
との接合強度が高い硼化物もしくは次回化物を第１図に
示すように主に粒界析出させる（この第１図において、
粒界析出物は主に硼化物もしくは炭硼化物７紋内析出物
は主に炭化物である。）ことにより、上記問題点の改善
をはかるようにすることも望ましい。Therefore, in a more preferred embodiment of the present invention, in view of these drawbacks, borides or borides, which have high bonding strength with the matrix due to their covalent bonding properties, are mainly used for grain boundary precipitation as shown in Figure 1. (In this Figure 1,
The grain boundary precipitates are mainly boride or carbide.7 The intra-grain precipitates are mainly carbides. ), it is also desirable to try to improve the above problems.
（実施例〕
以下、本発明による耐摩耗性鉄基焼結合金の実施例を比
較例と対比しながら説明する。(Examples) Examples of wear-resistant iron-based sintered alloys according to the present invention will be described below while comparing them with comparative examples.
原料粉末として、真空焼鈍を施した粒度−１００メッシ
、ノＦｅ−Ｃｒ−Ｍｏ −Ｗ−Ｓ ｉ −Ｃ系アトマイ
ズ合金粉末、−３２５メツシユのＦ ｅ −Ｍ ｏ粉末
あるいはＭＯ粒粉末−３２５メツシユのＦｅ−Ｗ粉末あ
るいはＷ粉末。As the raw material powder, vacuum annealed Fe-Mo powder with a grain size of -100 mesh, Fe-Cr-Mo-W-Si-C atomized alloy powder, -325 mesh Fe-Mo powder, or MO grain powder with a -325 mesh grain size is used. Fe-W powder or W powder.
−２５０メッシ、ｃ７）Ｆｅ−Ｂ合金粉末（８，２０％
含有）、−２５０メツシユのＦｅ−Ｐ合金粉末（Ｐ：２
６％含有）等を第２表に示す最終成分組成を持つように
適宜配合し、潤滑剤としてステアリン酩亜鉛を加えて混
合し、この混合粉末を７ｔｏｎｆ／Ｃｍ２の圧力で圧粉
体に成形し、ついで前記圧粉体を真空中で焼結した後焼
入れ焼戻し比較例合金Ｎｏ、 ７〜１１を製造した。-250 mesh, c7) Fe-B alloy powder (8,20%
), -250 mesh Fe-P alloy powder (P:2
(containing 6%) etc. were appropriately blended to have the final component composition shown in Table 2, and stearin-drunk zinc was added as a lubricant and mixed, and this mixed powder was molded into a green compact at a pressure of 7 tonf/Cm2. Then, the green compact was sintered in vacuum, and then quenched and tempered to produce Comparative Example Alloys Nos. 7 to 11.
ついで、得られた本発明実施例合金および比較例合金を
それぞれロッカアームのカムシャフトとの摺動部のチッ
プに使用し４気筒ＯＨＣガソリンエンジンにそれぞれ組
み込み、第３表に示す運転条件で耐久試験を行った。Next, the obtained alloys of the example of the present invention and the alloy of the comparative example were each used for the tip of the sliding part of the rocker arm with the camshaft, and were incorporated into a 4-cylinder OHC gasoline engine, and a durability test was conducted under the operating conditions shown in Table 3. went.
また、第２表には比較の目的で、従来材であるチル鋳鉄
製ロッカアームと、Ｆｅ−１２Ｃｒ−Ｃ系焼結合金製ロ
ッカアームについても同一の条件で耐久試験を行った結
、果を示した。In addition, for the purpose of comparison, Table 2 shows the results of durability tests conducted under the same conditions for rocker arms made of conventional chilled cast iron and rocker arms made of Fe-12Cr-C sintered alloy. .
そして、各耐久試験後のロッカアームチ・ンプとカムノ
ーズトップの最大摩耗深さを測定した。この結果を第２
図に示す。The maximum wear depth of the rocker arm tip and cam nose top after each durability test was then measured. This result is the second
As shown in the figure.
７〉−
第３表
第２図に示した結果より明らかなように、斤耗条件はき
わめて苛酷な条件で行われたために、従来材であるチル
鋳鉄（Ｎｏ、１４）とＦｅ−１２Ｃｒ−Ｃ系焼結合金（
Ｎｏ、１２．１３）はともにロッカアームチップおよび
カムともに摩耗量が著しく大きくなっている。7>- As is clear from the results shown in Table 3, Figure 2, the wear conditions were extremely severe, so the conventional materials, chilled cast iron (No. 14) and Fe-12Cr-C based sintered alloy (
No. 12.13), the amount of wear on both the rocker arm tip and the cam was significantly large.
また、比較例合金Ｎｏ、 ７ 、８のように、粒径２０
ｇｍ以上の硬質析出物を持つものでは、カムに対する攻
撃性が著しく増加してしまう。In addition, as in Comparative Example Alloy Nos. 7 and 8, the grain size was 20.
If the hard precipitate is larger than gm, the aggressiveness against the cam will increase significantly.
一方、比較例合金Ｎｏ、 ９のように、Ｂ丑が０．５重
量％未満でかつ硬質析出物の面積率が１０％未満になる
と、チップ自身の摩耗量が著しく大きくなるとともにカ
ムをも摩耗させてしまう。On the other hand, when the B content is less than 0.5% by weight and the area ratio of hard precipitates is less than 10%, as in Comparative Example Alloy No. 9, the amount of wear on the tip itself becomes significantly large and the cam is also worn out. I'll let you.
他方、Ｂ量が２．０重量％を超えると、焼結時にＢ系の
液相が多量に発生するために、粒界に共晶組織が形成さ
れ、材料自体が脆くなるので、比較例合金Ｎｏ、１０の
ように、チップ摩耗量が大きくなるだけでなく、カムに
対する攻撃性も非常に大きくなってしまう。On the other hand, if the amount of B exceeds 2.0% by weight, a large amount of B-based liquid phase will be generated during sintering, and a eutectic structure will be formed at the grain boundaries, making the material itself brittle. As in No. 10, not only the chip wear amount becomes large, but also the aggressiveness against the cam becomes very large.
また、比較例合金Ｎｏ、１１のように、Ｍｏ量が３０重
量％を超えてしまうと、粒径が２０ｇｍを超える硬質析
出物を生ずるとともに、材料自体が脆くなるために、カ
ムに対する攻撃性が非常に大きくなってしまう。In addition, when the Mo amount exceeds 30% by weight, as in Comparative Example Alloy No. 11, hard precipitates with a grain size exceeding 20 gm are formed, and the material itself becomes brittle, resulting in aggressiveness to the cam. It becomes very large.
これらに対して、本発明実施例合金Ｎｏ、 １〜６の
場合には、いずれも優れた＃摩耗性を示すほか、相手材
であるカムへの攻撃性も小さく、ロッカアームチップと
して非常に優れた特性を有していることがわかる。On the other hand, in the case of alloys Nos. 1 to 6 according to the present invention, they all exhibited excellent wear resistance and had little attack on the mating material, the cam, making them excellent as rocker arm tips. It can be seen that it has certain characteristics.
なお、前記実施例では本発明合金をロッカアームの摺動
部のチップに適用した場合について述へたが、タペット
、カム、スリーブおよびバルブシートなどの高血圧のか
かる用途に使用しても同様にすぐれた耐摩耗性を示すも
のである。In the above example, the alloy of the present invention was applied to the tip of the sliding part of a rocker arm, but it is equally effective when used in applications where high blood pressure is involved, such as tappets, cams, sleeves, and valve seats. It shows wear resistance.
［発明の効果］
上述のように、本発明による鉄基焼結合金は、重量比で
、ＭＯおよびＷのいずれか１種または２種；５〜３０％
、Ｃｒ； １０％以下、Ｓｉ；０．１〜０．９％、Ｍｎ
；０．７％以下、Ｐ；０．０５％以下、Ｃ；０．１〜２
．０％、Ｂ；０．５〜２．０％、残部Ｆｅおよび不純物
よりなる組成を有し、ベイナイトおよび／または焼もど
しマルテンサイトよりなるマトリックスに、粒径ｌｐｍ
以上２０４ｍ以下の微細な硼化物もしくは炭硼化物と炭
化物が共存していてこれらの硬質析出物が面積比で１０
％以上分散した組織を有するものであるから、耐摩耗性
、＃スカッフィング性および耐ピツチング性に著しく優
れるだけでなく、硼化物、炭硼化物のもつ良好ななじみ
性により相手材への攻撃性も著しく小さいという、１耐
摩耗材料として非常に好ましい特性を有するものである
。[Effects of the Invention] As described above, the iron-based sintered alloy according to the present invention contains one or two of MO and W in a weight ratio of 5 to 30%.
, Cr; 10% or less, Si; 0.1 to 0.9%, Mn
; 0.7% or less, P; 0.05% or less, C; 0.1-2
．． 0%, B: 0.5-2.0%, the balance is Fe and impurities, and the matrix is composed of bainite and/or tempered martensite, with a grain size lpm.
Fine borides or carbides and carbides with a size of 204 m or more coexist, and these hard precipitates have an area ratio of 10
% or more, it not only has outstanding wear resistance, #scuffing resistance, and pitting resistance, but also has good compatibility with boride and carboride, making it less aggressive to mating materials. It has very desirable characteristics as a wear-resistant material, such as being extremely small.
第１図はこの発明による鉄基耐摩耗性焼結合金の金属組
織を示す顕微鏡写真、第２図は耐久試験結果を示すグラ
フである。
特許出願人 日産自動車株式会社
特許出願人 日立粉末冶金株式会社
代理人弁理士 小 塩 豊
手系ゾごネ市正書
昭和６１年０９月０９日
特１作庁長官 黒田明雄殿
１、事件の表示
昭和６１年特許願第１８７４７１号
２、発明の名称
耐摩耗性鉄基焼結合金
３、補正をする者
事件との関係 特許出願人
氏名（名称） （３９８） 日産自動車株式会社氏名（
名称） 日立粉末冶金株式会社４、代理人
住所（居所）〒１０４東京都中央区銀座二丁目８番９号
木挽館銀座ビル 電話０３（５ｆｔ？）２７８１番（代
表）電写０３（５［１７）７９３３番（Ｇｉｎ）６、補
正により増加する発明の数
７、補正の対象
委任状、
明細書の発明の詳細な説明の欄
■、明細書第２頁第８行の「ロッカアーム」をｒロッカ
ーアーム」に補正する。
２、同第２頁第１５行の「ロッカアーム」を「ロッカー
アーム」に補正する。
３、同第２頁第１９行のｒロッカアーム」を「ロッカー
アーム」に補正する。
４、同第３頁第５行、第１４行〜第１５行。
第１６行、第２０行の「ロッカアーム」を「ロッカーア
ーム」に補正する。
５、同第４頁第２行の「ロッカアーム」を「ロッカーア
ーム」に補正する。
６、同第５頁第９行の「ロッカアーム」を「ロッカーア
ーム」に補正する。
７、同第６頁第１３行〜第１４行、第１６行の「ロッカ
アーム」を「ロッカーアーム」に補正する。
８、同第１０頁第１０行第１１行の「酎なじみ性」を「
なじみ性」に補正する。
９、同第１２頁第２行の「ロッカアーム」を「ロッカー
アーム」に補正する。
１１行の「ロッカアーム」を「ロッカーアーム」に補正
する。
１１、同第２０頁第１５行の「ロッカアーム」を「ロッ
カーアーム」に補正する。
１２、同第２１頁第１８行〜第１９行の「ロッカアーム
」ヲ「ロッカーアーム」に補正する。
１３、同第２２頁第１行〜第２行の「ロッカアーム」を
「ロッカーアーム」に補正する。
以 上FIG. 1 is a micrograph showing the metal structure of the iron-based wear-resistant sintered alloy according to the present invention, and FIG. 2 is a graph showing the results of a durability test. Patent Applicant Nissan Motor Co., Ltd. Patent Applicant Hitachi Powder Metallurgy Co., Ltd. Representative Patent Attorney Shio Ko Tekei Zogone City Sho Sho September 9, 1986 Special 1 Works Agency Commissioner Akio Kuroda 1, Incident Indication 1985 Patent Application No. 187471 2, Name of the invention: Wear-resistant iron-based sintered alloy 3, Relationship with the case of the person making the amendment Name of patent applicant (name) (398) Name of Nissan Motor Co., Ltd. (
Name) Hitachi Powder Metallurgy Co., Ltd. 4, Agent address (residence) Kobikikan Ginza Building, 2-8-9 Ginza, Chuo-ku, Tokyo 104 Telephone: 03 (5ft?) 2781 (Representative) Telegraph: 03 (5[17] ) No. 7933 (Gin) 6, Number of inventions increased by amendment 7, Power of attorney subject to amendment, Detailed explanation column of the invention in the specification ■, "Rocker arm" on page 2, line 8 of the specification is changed to r locker Correct to "arm". 2. Correct "rocker arm" in line 15 of page 2 to "rocker arm". 3. Correct "r rocker arm" in line 19 of page 2 to "rocker arm". 4, page 3, line 5, line 14 to line 15. Correct "rocker arm" in lines 16 and 20 to "rocker arm". 5. Correct "rocker arm" in the second line of page 4 to "rocker arm". 6. Correct "rocker arm" in line 9 of page 5 to "rocker arm". 7. Correct "rocker arm" in lines 13 to 14 and line 16 of page 6 to "rocker arm." 8. Change "Shochu familiarity" on page 10, line 10, line 11 to "
Correct for "familiarity". 9. Correct "rocker arm" in the second line of page 12 to "rocker arm". Correct "rocker arm" in line 11 to "rocker arm". 11. Correct "rocker arm" in line 15 of page 20 to "rocker arm". 12. Correct "rocker arm" in lines 18 to 19 of page 21 to "rocker arm". 13. Correct "rocker arm" in the first and second lines of page 22 to "rocker arm". that's all
Claims (2)
種：５〜３０％、Ｃｒ；１０％以下、Ｓｉ；０．１〜０
．９％、Ｍｎ；０．７％以下、Ｐ；０．０５％以下、Ｃ
；０．１〜２．０％、Ｂ；０．５〜２．０％、残部Ｆｅ
および不純物からなる組成を有し、ベイナイトおよび／
または焼もどしマルテンサイトよりなるマトリックスに
、粒径１μｍ以上２０μｍ以下の微細な硼化物もしくは
炭硼化物と炭化物が共存していてこれらの硬質析出物が
面積比で１０％以上分散した組織を有することを特徴と
する耐摩耗性鉄基焼結合金。(1) Any one or two of Mo and W in weight ratio
Species: 5-30%, Cr; 10% or less, Si; 0.1-0
．． 9%, Mn; 0.7% or less, P; 0.05% or less, C
; 0.1 to 2.0%, B; 0.5 to 2.0%, balance Fe
It has a composition consisting of bainite and/or impurities.
Or, a matrix consisting of tempered martensite has a structure in which fine borides or carbides and carbides with a grain size of 1 μm or more and 20 μm or less coexist, and these hard precipitates are dispersed in an area ratio of 10% or more. A wear-resistant iron-based sintered alloy featuring:
、Ｃｒ）からなり、炭化物は主に Ｍ＿６Ｃ（Ｍは、Ｆｅ、Ｍｏ、Ｗ）とＭ＿７Ｃ＿３（Ｍ
は、Ｆｅ、Ｃｒ）からなり、炭硼化物はＭ＿６Ｃ炭化物
を析出サイトとして形成されたＭ＿３（Ｂ、Ｃ）＿２（
Ｍは、Ｆｅ、Ｍｏ、Ｗ、Ｃｒ）であるこを特徴とする特
許請求の範囲第（１）項記載の耐摩耗性鉄基焼結合金。(2) Borides are mainly M_3B_2 (M is Fe, Mo, W
, Cr), and the carbides are mainly M_6C (M is Fe, Mo, W) and M_7C_3 (M
is composed of Fe, Cr), and carboride is M_3(B,C)_2( formed using M_6C carbide as a precipitation site)
The wear-resistant iron-based sintered alloy according to claim (1), wherein M is Fe, Mo, W, Cr).
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61187471A JPH07113141B2 (en) | 1986-08-08 | 1986-08-08 | Abrasion resistant iron-based sintered alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61187471A JPH07113141B2 (en) | 1986-08-08 | 1986-08-08 | Abrasion resistant iron-based sintered alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS6342357A true JPS6342357A (en) | 1988-02-23 |
| JPH07113141B2 JPH07113141B2 (en) | 1995-12-06 |
Family
ID=16206662
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61187471A Expired - Lifetime JPH07113141B2 (en) | 1986-08-08 | 1986-08-08 | Abrasion resistant iron-based sintered alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH07113141B2 (en) |
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0983555A (en) * | 1995-09-11 | 1997-03-28 | Hoei Shoji:Kk | Transmission controller for terminal equipment |
| US7749298B2 (en) | 2003-08-28 | 2010-07-06 | Toyota Jidosha Kabushiki Kaisha | Iron-based sintered alloy and manufacturing method thereof |
| CN107532265A (en) * | 2014-12-16 | 2018-01-02 | 思高博塔公司 | Toughness and wear-resistant ferrous alloy containing a variety of hard phases |
| JP2018503739A (en) * | 2014-12-17 | 2018-02-08 | ウッデホルムズ アーベー | Wear resistant alloy |
| JP2018532880A (en) * | 2015-09-04 | 2018-11-08 | スコペルタ・インコーポレイテッドＳｃｏｐｅｒｔａ， Ｉｎｃ． | Non-chromium and low chromium wear resistant alloys |
| WO2019191400A1 (en) * | 2018-03-29 | 2019-10-03 | Oerlikon Metco (Us) Inc. | Reduced carbides ferrous alloys |
| US11085102B2 (en) | 2011-12-30 | 2021-08-10 | Oerlikon Metco (Us) Inc. | Coating compositions |
| SE2130297A1 (en) * | 2021-11-05 | 2023-05-06 | Uddeholms Ab | A wear resistant alloy |
| US11939646B2 (en) | 2018-10-26 | 2024-03-26 | Oerlikon Metco (Us) Inc. | Corrosion and wear resistant nickel based alloys |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS55145156A (en) * | 1979-04-26 | 1980-11-12 | Nippon Piston Ring Co Ltd | Sintered alloy material for internal combustion engine |
| JPS57108246A (en) * | 1980-12-24 | 1982-07-06 | Hitachi Powdered Metals Co Ltd | Member of moving valve mechanism of internal combustion engine |
| JPS5916952A (en) * | 1982-07-20 | 1984-01-28 | Mitsubishi Metal Corp | Fe-based sintered material excellent in wear resistance |
| JPS6169946A (en) * | 1984-09-13 | 1986-04-10 | Toyota Motor Corp | Valve system sliding member and its manufacture |
-
1986
- 1986-08-08 JP JP61187471A patent/JPH07113141B2/en not_active Expired - Lifetime
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS55145156A (en) * | 1979-04-26 | 1980-11-12 | Nippon Piston Ring Co Ltd | Sintered alloy material for internal combustion engine |
| JPS57108246A (en) * | 1980-12-24 | 1982-07-06 | Hitachi Powdered Metals Co Ltd | Member of moving valve mechanism of internal combustion engine |
| JPS5916952A (en) * | 1982-07-20 | 1984-01-28 | Mitsubishi Metal Corp | Fe-based sintered material excellent in wear resistance |
| JPS6169946A (en) * | 1984-09-13 | 1986-04-10 | Toyota Motor Corp | Valve system sliding member and its manufacture |
Cited By (16)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0983555A (en) * | 1995-09-11 | 1997-03-28 | Hoei Shoji:Kk | Transmission controller for terminal equipment |
| US7749298B2 (en) | 2003-08-28 | 2010-07-06 | Toyota Jidosha Kabushiki Kaisha | Iron-based sintered alloy and manufacturing method thereof |
| US11085102B2 (en) | 2011-12-30 | 2021-08-10 | Oerlikon Metco (Us) Inc. | Coating compositions |
| CN107532265A (en) * | 2014-12-16 | 2018-01-02 | 思高博塔公司 | Toughness and wear-resistant ferrous alloy containing a variety of hard phases |
| CN107532265B (en) * | 2014-12-16 | 2020-04-21 | 思高博塔公司 | Ductile and wear resistant iron alloy containing multiple hard phases |
| US11242581B2 (en) | 2014-12-17 | 2022-02-08 | Uddeholms Ab | Wear resistant alloy |
| JP2018503739A (en) * | 2014-12-17 | 2018-02-08 | ウッデホルムズ アーベー | Wear resistant alloy |
| CN110699613B (en) * | 2014-12-17 | 2022-05-17 | 尤迪霍尔姆斯有限责任公司 | Wear-resistant alloy |
| CN110699613A (en) * | 2014-12-17 | 2020-01-17 | 尤迪霍尔姆斯有限责任公司 | Wear-resistant alloy |
| JP2018532880A (en) * | 2015-09-04 | 2018-11-08 | スコペルタ・インコーポレイテッドＳｃｏｐｅｒｔａ， Ｉｎｃ． | Non-chromium and low chromium wear resistant alloys |
| US11253957B2 (en) | 2015-09-04 | 2022-02-22 | Oerlikon Metco (Us) Inc. | Chromium free and low-chromium wear resistant alloys |
| WO2019191400A1 (en) * | 2018-03-29 | 2019-10-03 | Oerlikon Metco (Us) Inc. | Reduced carbides ferrous alloys |
| US11939646B2 (en) | 2018-10-26 | 2024-03-26 | Oerlikon Metco (Us) Inc. | Corrosion and wear resistant nickel based alloys |
| SE2130297A1 (en) * | 2021-11-05 | 2023-05-06 | Uddeholms Ab | A wear resistant alloy |
| WO2023080832A1 (en) * | 2021-11-05 | 2023-05-11 | Uddeholms Ab | A wear resistant alloy |
| SE545337C2 (en) * | 2021-11-05 | 2023-07-11 | Uddeholms Ab | A wear resistant alloy |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH07113141B2 (en) | 1995-12-06 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP3520093B2 (en) | Secondary hardening type high temperature wear resistant sintered alloy | |
| US5031878A (en) | Valve seat made of sintered iron base alloy having high wear resistance | |
| KR101245069B1 (en) | A powder metal engine composition | |
| JP2506333B2 (en) | Abrasion resistant iron-based sintered alloy | |
| US4360383A (en) | Abrasion resistant sintered alloy for internal combustion engines | |
| JP2001050020A (en) | Valve device for internal combustion engine | |
| JP2018529015A (en) | Tribology system including valve seat ring and valve | |
| JPH0350824B2 (en) | ||
| JP3784926B2 (en) | Ferrous sintered alloy for valve seat | |
| JPS6342357A (en) | Wear-resistant ferrous sintered alloy | |
| JPH0360901B2 (en) | ||
| JPS6070163A (en) | Wear resistant sintered alloy member | |
| JPS63274740A (en) | Wear resistant iron based sintered alloy | |
| JPH0116297B2 (en) | ||
| JPS63290249A (en) | Ferrous sintered alloy combining heat resistance with wear resistance | |
| JPH06179937A (en) | Sintered alloy for valve seat | |
| JPS6033343A (en) | Wear resistance sintered alloy | |
| JP2001234305A (en) | Sintered member | |
| JP3440008B2 (en) | Sintered member | |
| JP2594505B2 (en) | Rocker arm | |
| JP3187975B2 (en) | Sintered alloy for sliding members with excellent scuffing and wear resistance | |
| JPH0140101B2 (en) | ||
| JPH0561346B2 (en) | ||
| JPS6176650A (en) | Wear resistant sintered alloy | |
| JPS62167860A (en) | Combination of cam nose material and rocker pad material |