JPS6365056A - Wear resistant sintered iron alloy - Google Patents
Wear resistant sintered iron alloyInfo
- Publication number
- JPS6365056A JPS6365056A JP20997686A JP20997686A JPS6365056A JP S6365056 A JPS6365056 A JP S6365056A JP 20997686 A JP20997686 A JP 20997686A JP 20997686 A JP20997686 A JP 20997686A JP S6365056 A JPS6365056 A JP S6365056A
- Authority
- JP
- Japan
- Prior art keywords
- matrix
- sliding
- wear
- less
- members
- 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
- 229910000640 Fe alloy Inorganic materials 0.000 title abstract 3
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 14
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 13
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 11
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 11
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 10
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 8
- 229910052735 hafnium Inorganic materials 0.000 claims abstract description 6
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 6
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 6
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 5
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 5
- 229910045601 alloy Inorganic materials 0.000 claims description 37
- 239000000956 alloy Substances 0.000 claims description 37
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 34
- 229910052742 iron Inorganic materials 0.000 claims description 18
- 229910052721 tungsten Inorganic materials 0.000 claims description 14
- 239000012535 impurity Substances 0.000 claims description 5
- 239000011159 matrix material Substances 0.000 abstract description 22
- 239000000463 material Substances 0.000 abstract description 13
- 238000002485 combustion reaction Methods 0.000 abstract description 6
- 239000010687 lubricating oil Substances 0.000 abstract description 4
- 230000007547 defect Effects 0.000 abstract 1
- 239000000843 powder Substances 0.000 description 21
- 230000000694 effects Effects 0.000 description 15
- 150000001247 metal acetylides Chemical class 0.000 description 13
- 230000013011 mating Effects 0.000 description 12
- 230000007423 decrease Effects 0.000 description 8
- 239000000203 mixture Substances 0.000 description 8
- 239000003921 oil Substances 0.000 description 7
- 238000000137 annealing Methods 0.000 description 4
- 238000005245 sintering Methods 0.000 description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- 229910001563 bainite Inorganic materials 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 229910052760 oxygen Inorganic materials 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 229910000521 B alloy Inorganic materials 0.000 description 2
- 229910017086 Fe-M Inorganic materials 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 229910001562 pearlite Inorganic materials 0.000 description 2
- 239000011148 porous material Substances 0.000 description 2
- 238000005496 tempering Methods 0.000 description 2
- 229910000968 Chilled casting Inorganic materials 0.000 description 1
- 229910017060 Fe Cr Inorganic materials 0.000 description 1
- 229910002544 Fe-Cr Inorganic materials 0.000 description 1
- 229910001200 Ferrotitanium Inorganic materials 0.000 description 1
- 229910017116 Fe—Mo Inorganic materials 0.000 description 1
- -1 OS% or less Inorganic materials 0.000 description 1
- 229910001096 P alloy Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 125000002915 carbonyl group Chemical group [*:2]C([*:1])=O 0.000 description 1
- UPHIPHFJVNKLMR-UHFFFAOYSA-N chromium iron Chemical compound [Cr].[Fe] UPHIPHFJVNKLMR-UHFFFAOYSA-N 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 229910052731 fluorine Inorganic materials 0.000 description 1
- 239000000314 lubricant Substances 0.000 description 1
- 230000001050 lubricating effect Effects 0.000 description 1
- 238000005461 lubrication Methods 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 239000002699 waste material Substances 0.000 description 1
- XOOUIPVCVHRTMJ-UHFFFAOYSA-L zinc stearate Chemical compound [Zn+2].CCCCCCCCCCCCCCCCCC([O-])=O.CCCCCCCCCCCCCCCCCC([O-])=O XOOUIPVCVHRTMJ-UHFFFAOYSA-L 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ーアームやタペット等の
高面圧のかかる摺動部に使用した場合において、たとえ
カムとロッカーアームまたはタペットとの間の油膜が消
失して、カムとロッカーアームまたはタペットとが直接
接触したとしても、すぐれた耐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 high surface pressure parts such as rocker arms and tappets of internal combustion engines. Excellent wear resistance and conformability even if the oil film between the cam and rocker arm or tappet disappears and the cam comes into direct contact with the rocker arm or tappet. This relates to an iron-based sintered alloy that exhibits the following properties.
（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、特にロッカー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 rocker arms and tappets with the camshaft. The requirements for durability have become extremely strict.
一般に、ロッカー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。In general, the sliding parts of rocker arms and tappets that touch the camshaft are subject to high surface pressure, so it has excellent wear resistance, scuffing resistance, pitting resistance, and compatibility with the camshaft. required to have.
そこで、本発明者らは前記の事情にかんがみて、すでに
出願した特願昭６１−５４１５０号の明細書において、
マトリクス中に微細な炭化物と硼化物および／または炭
硼化物とが均一に分散している組織を有していて、とく
に内燃機関の摺動部材に適する耐摩耗性鉄基焼結合金の
発明を開示した。Therefore, in view of the above circumstances, the present inventors wrote in the specification of Japanese Patent Application No. 61-54150, which has already been filed.
We have invented a wear-resistant iron-based sintered alloy that has a structure in which fine carbides, borides, and/or carborides are uniformly dispersed in a matrix, and is particularly suitable for sliding members of internal combustion engines. Disclosed.
この特願昭６１−５４１５０号の発明による耐摩耗性鉄
基焼結合金では、所定の組織を得るために、重量％で、
ＭｏおよびＷのいずれか１種または２種；５〜２０％、
Ｃｒ；２〜１０％、Ｓｉ；０．１〜０．９％、Ｍｎ；０
．７％以下、 Ｐ；０．０５以下、Ｃ，０，１〜０．８
％、Ｂ；０．５〜２．０％、および必要に応じてＶ。In the wear-resistant iron-based sintered alloy according to the invention of Japanese Patent Application No. 61-54150, in order to obtain a predetermined structure, in weight %,
Any one or two of Mo and W; 5 to 20%,
Cr; 2-10%, Si; 0.1-0.9%, Mn; 0
．． 7% or less, P; 0.05 or less, C, 0.1 to 0.8
%, B; 0.5-2.0%, and V as necessary.
Ｎｂ、Ｔａ、Ｔｉ、Ｚｒ、Ｈｆ、Ｃｏ、Ｎｉのうちの１
種以上：２０％以下、残部Ｆａおよび不純物からなる組
成としたことを特徴としているものである。One of Nb, Ta, Ti, Zr, Hf, Co, Ni
The composition is characterized by having a composition consisting of at least 20% of species: 20% or less, and the remainder consisting of Fa and impurities.
（発明が解決しようとする問題点）
上記した特願昭６１−５４１５０号の発明による耐摩耗
性鉄基焼結合金では、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、相手材
とのなじみ性をも合わせて持つものであるため、ロッカ
ーアームやタペットとして通常使用する場合は全く問題
なく、かなり優れた特性を示すが、とくにエンジンの高
出力化等のために弁開閉の速度が大きくなり、カムプロ
フィールの立ち上りがきびしくなってカムとロッカーア
ームまたはタペットとの間で潤滑膜が消失して（すなわ
ち、油膜切れして）カムとロッカーアームまたはタペッ
トとが高面圧下で直接的に接触する場合には、Ｃ含有量
が０．１〜０．８重量％であるように規制したためにマ
トリクス中の炭化物量がやや少ないので、スカッフィン
グを起すこともありうるという問題点のあることがわか
った。(Problems to be Solved by the Invention) The wear-resistant iron-based sintered alloy according to the invention of Japanese Patent Application No. 61-54150 mentioned above not only has excellent wear resistance, scuffing resistance, and pitting resistance. Since it also has compatibility with the mating material, there is no problem when used normally as a rocker arm or tappet, and it shows quite excellent characteristics, but it is especially suitable for valves for high engine output, etc. The opening/closing speed increases, the rise of the cam profile becomes severe, and the lubricating film between the cam and the rocker arm or tappet disappears (i.e., the oil film runs out), causing the cam and the rocker arm or tappet to be under high surface pressure. In the case of direct contact, the amount of carbide in the matrix is somewhat small because the C content is regulated to be 0.1 to 0.8% by weight, so there is a problem that scuffing may occur. It turns out that there is.
（発明の目的）
そこで、本発明者らは油切れ時にカムとロッカーアーム
またはタペットとが高面圧下で直接的に接触したとして
も、スカッフィングが起きないようにすることを目的と
して種々の実験、研究を行った結果、Ｃ含有量を０．８
超過〜２．０重量％に増量し、マトリクス内の炭化物を
粗大化させることなく増加させることにより、油膜切れ
時にカムとロッカーアームまたはタペットとが高面圧下
で直接的に接触したとしても、スカッフィングを起しに
くくなることを見い出して本発明を完成するに至った。(Object of the Invention) Therefore, the present inventors conducted various experiments with the aim of preventing scuffing from occurring even if the cam and the rocker arm or tappet come into direct contact under high surface pressure when the oil runs out. As a result of research, the C content was reduced to 0.8
By increasing the amount to 2.0% by weight and increasing the carbide in the matrix without coarsening it, scuffing is prevented even if the cam and rocker arm or tappet come into direct contact under high surface pressure when the oil film runs out. The present invention was completed based on the discovery that this phenomenon is less likely to occur.
［発明の構成］
（問題点を解決するための手段）
本発明の第一発明による耐摩耗性鉄基焼結合金は、重量
％で、ＭｏおよびＷのいずれか１種または２種：５〜２
０％、Ｃｒ；２〜１０％、Ｓｉ；０．１〜０．９％、Ｍ
ｎ ； ０ 、７％以下、Ｐ；Ｏ，ＯＳ％以下、Ｃ；
Ｏ，ａ超過〜２．０％、Ｂ；０．５〜２．０％、残部Ｆ
ｅおよび不純物からなることを特徴としている。[Structure of the Invention] (Means for Solving the Problems) The wear-resistant iron-based sintered alloy according to the first aspect of the present invention contains one or both of Mo and W in weight percent: 5 to 5. 2
0%, Cr; 2-10%, Si; 0.1-0.9%, M
n; 0, 7% or less, P; O, OS% or less, C;
O, excess a~2.0%, B; 0.5~2.0%, remainder F
It is characterized by consisting of e and impurities.
また、本発明の第二発明による耐摩耗性鉄基焼結合金は
、上記の組成に加えて、Ｖ、Ｎｂ。Further, the wear-resistant iron-based sintered alloy according to the second aspect of the present invention contains V and Nb in addition to the above composition.
Ｔａ、Ｔｉ 、Ｚｒ、Ｈｆ”、Ｃｏ、Ｎｉよりなる群か
ら選ばれた元素のうちの１種以上：２０％以下を含むこ
とを特徴としている。It is characterized by containing 20% or more of one or more elements selected from the group consisting of Ta, Ti, Zr, Hf'', Co, and Ni.
木発舅者等は、上記の組成をもつ耐摩耗性鉄基焼結合金
において、とくにマトリクス組織中に微細でかつ十分な
量の炭化物と、微細な硼化物および／または炭硼化物が
均一に分散している組織を有するものがすぐれた摺動摩
耗特性を有し、とりわけたとえばロッカーアームまたは
タペットの摺動部に使用した場合において、潤滑油膜が
消失してカムとロッカーアームまたはタペットとが直接
的に接触したとしても、スカッフィングなどの不具合が
起きることなく優れた摺動特性を発揮することを見いだ
した。Kiwaka et al. proposed that, in a wear-resistant iron-based sintered alloy with the above composition, a sufficient amount of fine carbide and fine boride and/or carboride are uniformly contained in the matrix structure. Those with a dispersed structure have excellent sliding wear properties, especially when used on sliding parts of rocker arms or tappets, for example, when the lubricating oil film disappears and the cam and rocker arm or tappet are directly connected. It was discovered that even when the material comes in contact with other surfaces, it exhibits excellent sliding characteristics without causing problems such as scuffing.
本発明は上記の知見に基づいてなされたものであり、以
下に成分組成（重量割合）を上記の通りに限定した理由
を説明する。The present invention has been made based on the above findings, and the reason why the component composition (weight ratio) is limited as described above will be explained below.
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
合して複炭化物や複硼化物あるいは復炭硼化物を形成し
て耐摩耗性を与え、一部はマトリクス内に固溶して当該
マトリ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、５％未満では所望の効果が得られずに耐摩
耗性不足となり、２０％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５〜２０％と定めた。Mo and W: Mo and W combine with C and B together with Fe and Cr in the components to form double carbides, complex borides, or double carbides to provide wear resistance, and some of them are solidified within the matrix. It melts to strengthen the matrix and has the effect of increasing tempering hardenability, but if it is less than 5%, the desired effect will not be obtained and wear resistance will be insufficient, and if it is contained in excess of 20%, further improvement will not occur. Since no effect was observed and it was not economical, the content was set at 5 to 20%.
Ｃｒ：
ＣｒはＭ ｏ 、 Ｗ等とともに複炭化物や複硼化物を
形成して耐摩耗性を向上させると同時に、マトリクス中
に固溶して焼入性を増大させ、さらには焼戻し硬化能を
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
効果もあるが、２％未満ではその効果が認められず、１
０％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有量を２〜１０％と定め
た。Cr: Cr forms double carbides and complex borides together with Mo, W, etc. to improve wear resistance, and at the same time, dissolves solidly in the matrix to increase hardenability and further improves temper hardening ability. It is effective and also has the effect of improving the corrosion resistance of the base, but if it is less than 2%, this effect is not recognized, and 1%
If the content exceeds 0%, not only will there be no further improvement effect, but the mechanical strength will decrease and the aggressiveness towards the mating material will increase, so the content is set at 2 to 10%. Ta.
Ｓ ｉ ：
Ｓｉ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。Si: When Si is added in an amount less than 0.1%, the deoxidizing effect is small, and the oxygen content in the powder increases, reducing sinterability and making M2C-based coarse plate-like carbides more likely to precipitate. , the compatibility with the mating member decreases. On the other hand, the amount added is 0.9
%, the deoxidizing effect will not be improved and the powder will become round and the moldability will be reduced. Therefore, the content was set at 0.1-0.9%.
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することにより成形体エツジ部
の欠は等が生じやすくなることから、添加するとしても
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. As a result, the moldability of the powder decreases, making it more likely to cause cracks on the edges of the compact, so the content, if added at all, 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０．２〜０．８％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、粒界に複硼化物あるいは復炭硼化物がネットワー
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ツ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 an amount of about 0.2 to 0.8%, but in the case of the sintered alloys of the present invention, P is If the amount added exceeds 0.05%, the complex boride or carbon boride becomes coarse and the compatibility with the mating material decreases, and the complex boride or carbon boride forms a network at the grain boundaries. The content was determined to be 0.05% or less because the steel precipitates 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、０．８％以下では
複炭化物の量が少なすぎ、またマトリクスの室温硬さも
小さすぎて、潤滑油膜を介在させない摺動状況では耐摩
耗性が不十分である。しかし、２．０％を超えると複炭
化物が凝集析出し、粗大な炭硼化物も生成して脆化しや
すくなるうえに、相手材とのなじみ性が低下することか
ら、その含有量を０．８超過〜２．０％と定めた。C; A part of C combines with carbide-forming elements such as Mo, W, Cr, and V to form double carbides to improve wear resistance, and the rest is dissolved in the matrix and has high room temperature hardness. However, if it is less than 0.8%, the amount of double carbides is too small and the room temperature hardness of the matrix is too small, resulting in insufficient wear resistance under sliding conditions without a lubricating oil film. . However, if it exceeds 2.0%, double carbides will coagulate and precipitate, and coarse carborides will also be generated, making them susceptible to embrittlement and reducing compatibility with the mating material, so the content should be reduced to 0.0%. It has been set as 2.0% over 8.
このＣの添加方法としては、真空焼鈍を施したＦｅ−Ｍ
ｏ −Ｗ−Ｃｒ−Ｖ−３ｉ −（Ｍｎ） −（Ｃｏ）−
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
させてしまうのに対して、真空焼鈍を施したＦ ｅ−Ｍ
ｏ −Ｗ−Ｃｒ−Ｖ−Ｓ ｉ −（Ｍｎ） −（Ｃｏ）
−Ｃ系アトマイズ合金粉末の形で添加した場合は、アト
マイズ後の真空焼鈍時にＣは大部分がＭ ｏ 、 Ｗ
、 Ｃｒ 、 Ｖ 、 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７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 this C, Fe-M subjected to vacuum annealing is
o -W-Cr-V-3i -(Mn)-(Co)-
It is necessary to add it in the form of C-based atomized alloy powder. If C is added alone in the form of graphite powder, Fe-B or Fe-Cr added as a B source (described later)
-When combined with B, coarse carborides are precipitated in a network along the grain boundaries during sintering, increasing the aggressiveness of the mating material, whereas Fe-M subjected to vacuum annealing
o -W-Cr-V-Si-(Mn)-(Co)
- When added in the form of a C-based atomized alloy powder, most of the C becomes Mo, W during vacuum annealing after atomization.
, Cr, V, Fe, etc., and are precipitated in the atomized alloy powder as fine double carbides. The double carbide in the part is Fe-B or Fe-
It combines with Cr-B to form a double carbide boride that is slightly larger than the original double carbide, and the fine double carbides within the grains remain as they are after sintering and combine with Fe-B and Fe-Cr-B. This is because a unique structure of the sintered alloy according to the present invention is obtained, in which fine complex borides generated by decomposition and precipitation between Mo and W in the Tomized alloy powder are uniformly dispersed.
Ｂ；
Ｂは成分中のＭ Ｏ、Ｗ 、 Ｖ 、 Ｃｒ 、 Ｆ
ｅとともに複硼化物を形成して＃摩耗性と耐なじみ性を
与えるとともに、一部はマトリクス中に固溶して焼入性
を改善する。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＃摩耗性を向上させる。B; B is MO, W, V, Cr, F in the components
Together with e, it forms a complex boride to provide wear resistance and conformability resistance, and a portion is dissolved in the matrix to improve hardenability. Further, a part of the above-mentioned complex boride is also combined with C to form a carbonized boride, which improves 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
り一層の改善効果は認められず、かえって複硼化物の粗
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０．５〜２．０％と定めた。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%, and no further improvement was observed with the addition of more than 2.0%, which instead caused the complex boride to become coarser and reduce its compatibility with the mating material. Its content was determined to be 0.5 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との間で、［Ｍｏ＋
Ｗ含有量（原子量）コ／［Ｂ含有量（原子量）］＝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。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。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 between M O + W. [Mo+
W content (atomic weight) / [B content (atomic weight)] = 0.
This is when the relationship of 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. becomes coarser and precipitates at grain boundaries in the form of a network,
This is because the compatibility with the mating material decreases, and at the same time, the pitting resistance of the material itself decreases. As for the method of adding B, it is preferable to add it in the form of Fe-B or Fe-Cr-B alloy powder.
Ｖ、Ｎｂ、Ｔａ；
Ｖ、Ｎｂ、ＴａはＦｅやＣｒとともにＣと結合してきわ
めて硬い複炭化物を作るとともに。V, Nb, Ta; V, Nb, and Ta combine with C together with Fe and Cr to form extremely hard double carbides.
Ｍｏ，Ｗの一部と置換した形の複炭化物や複硼化物を形
成して耐摩耗性を与え、一部はマトリクス中に固溶して
出該マトリ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。また■。Forms double carbides and complex borides in the form of partial substitution of Mo and W to provide wear resistance, and some solid dissolve in the matrix to strengthen the matrix and increase temper hardening ability. It has an effect. Also ■.
Ｎｂ、Ｔａは焼結時の結晶粒の粗大化を防止するととも
に炭化物の粗大化を防止する効果もある。Nb and Ta have the effect of preventing coarsening of crystal grains during sintering and also of preventing coarsening of carbides.
これらの効果はＶ、Ｎｂ、Ｔａが０．５％未満の場合で
はあまり認められず、耐摩耗性や強度の低下をきたし、
一方８％を超えて添加しても一層の改善効果は認められ
ず経済的でないことから、添加するとしてもその含有量
を０．５〜８％とするのが良い。These effects are not so noticeable when V, Nb, and Ta are less than 0.5%, resulting in a decrease in wear resistance and strength.
On the other hand, even if it is added in an amount exceeding 8%, no further improvement effect is observed and it is not economical, so even if it is added, it is preferable to limit its content to 0.5 to 8%.
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、Ｇｏ等を必要に応じて１２％以下の範囲
で添加しても良い、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、マトリクス中に
固溶して赤熱硬さを向上させるため、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, Go, etc. may be added in a range 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 forms a complex boride in the matrix. Since it improves red-hot hardness by forming a solid solution in it, it is particularly effective to add it when hot wear resistance is required.
また、マトリクスがオーステナイト化しない範囲でＮｉ
を添加しても良い、これはＮｉを添加するとマトリクス
の耐食性が向上するため、ディーゼルエンジンのＥＧＲ
仕様のロッカー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。In addition, Ni
This is because adding Ni improves the corrosion resistance of the matrix.
It is especially effective when applied to parts that are subject to severe corrosion and wear, such as specified rocker arms and hydraulic lifters.
本発明による焼結合金の硬さとしては、ＨＲＣ５０〜６
８の範囲が好ましい、これは、ＨＲＣ５０未満では耐摩
耗性が不足し、ＨＲＣ６８を超えると相手材とのなじみ
性が低下するためである。The hardness of the sintered alloy according to the present invention is HRC50 to 6.
The range of 8 is preferable because if the HRC is less than 50, the wear resistance is insufficient, and if the HRC is more than 68, the compatibility with the mating material decreases.
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, because if the theoretical density ratio is less than 90%, the strength of the matrix will be low and the pores will be large, and the matrix will be easily destroyed due to the notch action of these pores, resulting in pitting wear. This is because it is more likely to occur.
（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。(Example) 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−ｌ００メッシ
、（７）Ｆ ｅ−Ｃｒ−Ｍｏ −Ｗ−３ｉ −Ｃ系アト
マイズ合金粉末（必要に応じＶ、Ｎｂ。As raw material powder, particle size -100 mesh subjected to vacuum annealing, (7) Fe-Cr-Mo-W-3i-C-based atomized alloy powder (V, Nb as necessary).
Ｔａ、Ｃｏも添加）、−３２５メツシユのＦｅ−Ｍｏ粒
粉末るいは純Ｍｏ粉末、−３２５メツシュのＦｅ−Ｗ粉
末あるいは純Ｗ粉末、−２５０メッシ、（Ｆ）Ｆ ｅ−
Ｂ合金粉末（Ｂ ； ２０％含有）。Ta and Co are also added), -325 mesh Fe-Mo grain powder or pure Mo powder, -325 mesh Fe-W powder or pure W powder, -250 mesh, (F)Fe-
B alloy powder (B; 20% content).
−２５０メ−／ シュ（７） Ｆ ｅ −Ｐ合金粉末（
Ｐ；２６％含有）、−２５０メツシユのフェロチタン。-250m/sh (7) F e -P alloy powder (
P; 26% content), -250 mesh ferrotitanium.
フェロジルコニウム、フェロハフニウム喜合金粉末、−
３２５メツシュのカーボニルＮｉ粉末等を第１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
テアリン酸亜鉛を加えて混合し、この混合粉末を７ｔｏ
ｎｆ／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１１５０ Ｎ１２５０℃の温度にて６０分
間保持して焼結した後焼入れ焼戻し処理を行って本発明
実施例合金間、１〜１５および比較例会金陽、１〜１２
を製造した。Ferrozirconium, ferrohafnium alloy powder, −
325 mesh carbonyl Ni powder, etc. were appropriately blended to have the final component composition shown in Table 1, and zinc stearate was added as a lubricant and mixed.
The powder compact was formed into a green compact under a pressure of nf/cm2, and then the compact was sintered by holding it in a vacuum at a temperature of 1150 N and 1250°C for 60 minutes, followed by quenching and tempering to form the alloys of the embodiments of the present invention. , 1-15 and Comparative Meeting Kinyo, 1-12
was manufactured.
ついで、この結果得られた本発明実施例合金間、１〜１
５および比較例会金慟、１〜１０をそれぞれラッシュア
ジャスタ内蔵型のロッカーアームのカムシャフトとの摺
動部に使用し、４気筒ＤＯＨＣガソリンエンジンにそれ
ぞれ組み込み、カムシャフトはチル鋳物製で高出力用の
高リフトタイプのもので弁の開閉速度が大きくかつ低速
回転ではロッカーアームの摺動部との間で油膜切れを生
じやすいカムプロフィールをもったカムを使用した。そ
して、エンジン回転数；６００ｒｐｍ、オイル；ガソリ
ンエンジン用約２万Ｋｍ走行の廃油、運転時間；６００
時間、およびその他の条件は実際の市場走行と同一の条
件で摩耗試験を行ない、ロッカーアーム摺動部における
摩耗量および相手部材であるカムの摩耗量を測定すると
共に、同摺動部におけるスカッフィングおよびピッチン
グの発生状況を観察した。この結果を同第１表に示す結
果から明らかなように、比較例合金間、１〜１２で示し
たごとく、成分組成の範囲が本発明合金からはずれた合
金では、それぞれロッカーアームやカムシャフトの摩耗
が大きかったり、スカッフィングやピッチングの発生が
認められたりして、いずれも満足のできる特性は示して
いないことがわかった。Next, among the alloys of the present invention obtained as a result, 1 to 1
5 and Comparative Meeting Kinki, 1 to 10 are each used for the sliding part of the rocker arm with a built-in lash adjuster and the camshaft, and each is incorporated into a 4-cylinder DOHC gasoline engine, and the camshaft is made of chilled casting for high output. We used a high-lift type cam with a high valve opening/closing speed and a cam profile that tends to cause an oil film to run out between it and the sliding part of the rocker arm at low speeds. Engine speed: 600 rpm, oil: Waste oil for gasoline engine after traveling approximately 20,000 km, operating time: 600 rpm.
A wear test was conducted under the same time and other conditions as actual driving on the market, and the amount of wear on the rocker arm sliding part and the wear amount on the cam, which is the mating member, was measured, as well as scuffing and other problems on the sliding part. The occurrence of pitching was observed. As is clear from the results shown in Table 1, the comparison alloys and the alloys whose compositions deviate from those of the present invention alloys, as shown in 1 to 12, were found to be less effective in rocker arms and camshafts, respectively. It was found that none of them exhibited satisfactory characteristics, with large wear and occurrence of scuffing and pitting observed.
これに対して、本発明実施例合金間、１〜１５の場合は
いずれも優れた＃摩耗性を示し、相手部材であるカムを
損傷させることもなく、さらには耐スカッフィング性お
よび耐ピツチング性にもされあて優れたものとなってい
ることがわかった。On the other hand, the alloys 1 to 15 of the present invention exhibited excellent wear resistance, did not damage the mating member cam, and had excellent scuffing resistance and pitting resistance. It turned out that it was an excellent product.
なお、ここに示した本発明実施例合金は熱処理によって
マトリクス組織は焼戻しマルテンサイトを主体とするも
のとなっているが、この熱処理条件を適宜選、択するこ
とによって、マトリクスの組織をベイナイト、パーラ・
イト、ベイナイト＋パーライト等の組織とすることもで
きるのはもちろんである。The matrix structure of the example alloy of the present invention shown here is mainly composed of tempered martensite due to heat treatment, but by appropriately selecting the heat treatment conditions, the matrix structure can be changed to bainite or pearlite.・
Of course, it is also possible to have a structure of bainite, bainite + pearlite, etc.
なお、ここで示した実施例では、本発明実施例合金をロ
ッカーアームの摺動部に適用した場合について述べたが
、タペット、カム、スリーブおよびバルブシートなどの
ように、高面圧がかかるうえに境界潤滑ないしは乾燥摩
耗をするような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 example shown here, the case where the alloy of the present invention was applied to the sliding parts of rocker arms was described, but it was applied to the sliding parts of rocker arms, etc., which are subject to high surface pressure and are It also exhibits excellent wear resistance even when used in applications involving boundary lubrication or dry wear.
［発明の効果］
上述のように、本発明者等の第一発明による鉄基焼結合
金は、重量％で、ＭｏおよびＷのいずれか１種または２
種；５〜２０％、Ｃｒ；２〜１０％、Ｓｌ、０．１〜０
．９％、Ｍ ｎ ； ０ 、７％以下、Ｐ、０．０５％
以下、Ｃ；Ｏ，ａ超過〜２．０％、Ｂ、０．５〜２．０
％、残部Ｆｅおよび不純物よりなる組成を有するもので
あり、また第二発明による鉄基焼結合金は、上記の組成
に加えて、Ｖ、Ｎｂ、Ｔａ、Ｔｉ、Ｚｒ、Ｈｆ。[Effects of the Invention] As described above, the iron-based sintered alloy according to the first invention of the present inventors contains one or two of Mo and W in weight%.
Seed; 5-20%, Cr; 2-10%, Sl, 0.1-0
．． 9%, Mn; 0, 7% or less, P, 0.05%
Below, C: O, exceeding a ~ 2.0%, B, 0.5 ~ 2.0
%, the balance being Fe and impurities, and the iron-based sintered alloy according to the second invention contains V, Nb, Ta, Ti, Zr, and Hf in addition to the above composition.
Ｇｏ、Ｎｉよりなる群から選ばれた元素のうちの１種以
上：２０％以下を含むものであるため、上記いずれの発
明による鉄基焼結合金においても、マトリクス中に硬質
層として複硼化物と十分な量の複炭化物および／または
復炭硼化物を均一に分散させた組織とすることができる
。したがって、これらの合金を例えば高い面圧のかかる
用途に使用した場合に、前記面圧が前記硬質粒子によっ
て分散されるようになり、加えて、摺動の際に摺動部（
摺動面）同士が潤滑油膜等を介さずに直接的に接触した
としても、マトリクス中の十分な量の複炭化物が凝着を
阻止することができる。それゆえ、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示し、特に
、Ｖ、Ｎｂ、Ｔａのうちの１種以上を含有する鉄基合金
にあってはとくに優れた耐摩耗性、耐スカッフィング性
および耐ピツチング性を示し、さらには複硼化物および
／または復炭硼化物の憬れたなじみ性により、相手部材
の摩耗をも改善することができるなど、工業上極めて有
益な特性を有するものである。Since it contains 20% or less of one or more elements selected from the group consisting of Go and Ni, in the iron-based sintered alloy according to any of the above inventions, it is sufficient to form a hard layer in the matrix with complex boride. It is possible to obtain a structure in which a large amount of double carbide and/or double carbide boride is uniformly dispersed. Therefore, when these alloys are used, for example, in applications where high surface pressure is applied, the surface pressure is dispersed by the hard particles, and in addition, the sliding portion (
Even if the sliding surfaces (sliding surfaces) come into direct contact with each other without a lubricating oil film or the like, a sufficient amount of double carbide in the matrix can prevent adhesion. Therefore, excellent wear resistance,
It exhibits scuffing resistance and pitting resistance, and in particular, iron-based alloys containing one or more of V, Nb, and Ta exhibit particularly excellent wear resistance, scuffing resistance, and pitting resistance, Furthermore, due to the loose compatibility of the complex boride and/or the carbonated boride, it has extremely useful industrial properties, such as being able to improve the wear of the mating member.
Claims (2)
種；５〜２０％、Ｃｒ；２〜１０％、Ｓｉ；０．１〜０
．９％、Ｍｎ；０．７％以下、Ｐ；０．０５％以下、Ｃ
；０．８超過〜２．０％、Ｂ；０．５〜２．０％、残部
Ｆｅおよび不純物からな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%
Seed; 5-20%, Cr; 2-10%, Si; 0.1-0
．． 9%, Mn; 0.7% or less, P; 0.05% or less, C
A wear-resistant iron-based sintered alloy characterized by consisting of: exceeding 0.8 to 2.0%, B: 0.5 to 2.0%, and the balance consisting of Fe and impurities.
種；５〜２０％、Ｃｒ；２〜１０％、Ｓｉ；０．１〜０
．９％、Ｍｎ；０．７％以下、Ｐ；０．０５％以下、Ｃ
；０．８超過〜２．０％、Ｂ；０．５〜２．０％、およ
びＶ、Ｎｂ、Ｔａ、Ｔｉ、Ｚｒ、Ｈｆ、Ｃｏ、Ｎｉより
なる群から選ばれた元素のうちの１種以上：２０％以下
、残部Ｆｅおよび不純物からなることを特徴とする耐摩
耗性鉄基焼結合金。(2) Any one or two of Mo and W in weight%
Seed; 5-20%, Cr; 2-10%, Si; 0.1-0
．． 9%, Mn; 0.7% or less, P; 0.05% or less, C
; exceeding 0.8 to 2.0%, B; 0.5 to 2.0%, and one of the elements selected from the group consisting of V, Nb, Ta, Ti, Zr, Hf, Co, and Ni. A wear-resistant iron-based sintered alloy characterized in that the content is 20% or less, and the balance is Fe and impurities.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP20997686A JPS6365056A (en) | 1986-09-05 | 1986-09-05 | Wear resistant sintered iron alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP20997686A JPS6365056A (en) | 1986-09-05 | 1986-09-05 | Wear resistant sintered iron alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS6365056A true JPS6365056A (en) | 1988-03-23 |
Family
ID=16581798
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP20997686A Pending JPS6365056A (en) | 1986-09-05 | 1986-09-05 | Wear resistant sintered iron alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6365056A (en) |
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0659894A2 (en) * | 1993-12-27 | 1995-06-28 | Kabushiki Kaisha Toyota Chuo Kenkyusho | High-modulus iron-based alloy and a process for manufacturing the same |
| KR100234601B1 (en) * | 1996-04-15 | 1999-12-15 | 셈보쿠야 아키오 | High temperature wear resistant sintered alloy |
| JP2001279369A (en) * | 2000-03-30 | 2001-10-10 | Hitachi Metals Ltd | Wear resistant and corrosion resistant alloy and cylinder for molding machine |
| GB2441482A (en) * | 2003-07-31 | 2008-03-05 | Komatsu Mfg Co Ltd | Sintered sliding member and connecting device |
| WO2017040775A1 (en) | 2015-09-04 | 2017-03-09 | Scoperta, Inc. | Chromium free and low-chromium wear resistant alloys |
| US10173290B2 (en) | 2014-06-09 | 2019-01-08 | Scoperta, Inc. | Crack resistant hardfacing alloys |
| US10329647B2 (en) | 2014-12-16 | 2019-06-25 | Scoperta, Inc. | Tough and wear resistant ferrous alloys containing multiple hardphases |
| US11085102B2 (en) | 2011-12-30 | 2021-08-10 | Oerlikon Metco (Us) Inc. | Coating compositions |
| US11939646B2 (en) | 2018-10-26 | 2024-03-26 | Oerlikon Metco (Us) Inc. | Corrosion and wear resistant nickel based alloys |
Citations (2)
| 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 |
| JPS5822358A (en) * | 1981-07-30 | 1983-02-09 | Mitsubishi Metal Corp | Iron base sintered alloy for structural member of fuel supply apparatus |
-
1986
- 1986-09-05 JP JP20997686A patent/JPS6365056A/en active Pending
Patent Citations (2)
| 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 |
| JPS5822358A (en) * | 1981-07-30 | 1983-02-09 | Mitsubishi Metal Corp | Iron base sintered alloy for structural member of fuel supply apparatus |
Cited By (21)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0659894A3 (en) * | 1993-12-27 | 1995-11-15 | Toyoda Chuo Kenkyusho Kk | High-modulus iron-based alloy and a process for manufacturing the same. |
| EP0659894A2 (en) * | 1993-12-27 | 1995-06-28 | Kabushiki Kaisha Toyota Chuo Kenkyusho | High-modulus iron-based alloy and a process for manufacturing the same |
| KR100234601B1 (en) * | 1996-04-15 | 1999-12-15 | 셈보쿠야 아키오 | High temperature wear resistant sintered alloy |
| JP2001279369A (en) * | 2000-03-30 | 2001-10-10 | Hitachi Metals Ltd | Wear resistant and corrosion resistant alloy and cylinder for molding machine |
| JP4491758B2 (en) * | 2000-03-30 | 2010-06-30 | 日立金属株式会社 | Cylinder for molding machine |
| GB2441482A (en) * | 2003-07-31 | 2008-03-05 | Komatsu Mfg Co Ltd | Sintered sliding member and connecting device |
| GB2441482B (en) * | 2003-07-31 | 2008-09-03 | Komatsu Mfg Co Ltd | Sintered sliding member and connecting device |
| US11085102B2 (en) | 2011-12-30 | 2021-08-10 | Oerlikon Metco (Us) Inc. | Coating compositions |
| US10173290B2 (en) | 2014-06-09 | 2019-01-08 | Scoperta, Inc. | Crack resistant hardfacing alloys |
| US11130205B2 (en) | 2014-06-09 | 2021-09-28 | Oerlikon Metco (Us) Inc. | Crack resistant hardfacing alloys |
| US11111912B2 (en) | 2014-06-09 | 2021-09-07 | Oerlikon Metco (Us) Inc. | Crack resistant hardfacing alloys |
| US10329647B2 (en) | 2014-12-16 | 2019-06-25 | Scoperta, Inc. | Tough and wear resistant ferrous alloys containing multiple hardphases |
| CN108350528A (en) * | 2015-09-04 | 2018-07-31 | 思高博塔公司 | Chrome-free and low chromium antifriction 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 |
| US10105796B2 (en) * | 2015-09-04 | 2018-10-23 | Scoperta, Inc. | Chromium free and low-chromium wear resistant alloys |
| EP3344789A4 (en) * | 2015-09-04 | 2019-07-31 | Scoperta, Inc. | Chromium free and low-chromium wear resistant alloys |
| EP3344789A1 (en) * | 2015-09-04 | 2018-07-11 | Scoperta, Inc. | Chromium free and low-chromium wear resistant alloys |
| US20170066090A1 (en) * | 2015-09-04 | 2017-03-09 | Scoperta Inc. | Chromium free and low-chromium wear resistant alloys |
| WO2017040775A1 (en) | 2015-09-04 | 2017-03-09 | Scoperta, Inc. | Chromium free 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 |
| US11939646B2 (en) | 2018-10-26 | 2024-03-26 | Oerlikon Metco (Us) Inc. | Corrosion and wear resistant nickel based alloys |
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