JP3440008B2 - Sintered member - Google Patents
Sintered memberInfo
- Publication number
- JP3440008B2 JP3440008B2 JP34654198A JP34654198A JP3440008B2 JP 3440008 B2 JP3440008 B2 JP 3440008B2 JP 34654198 A JP34654198 A JP 34654198A JP 34654198 A JP34654198 A JP 34654198A JP 3440008 B2 JP3440008 B2 JP 3440008B2
- Authority
- JP
- Japan
- Prior art keywords
- mass
- sintered member
- sintered
- sintering
- resistance
- 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.)
- Expired - Fee Related
Links
- 229910001566 austenite Inorganic materials 0.000 claims description 31
- 239000011159 matrix material Substances 0.000 claims description 28
- 230000000717 retained effect Effects 0.000 claims description 27
- 229910000734 martensite Inorganic materials 0.000 claims description 11
- 229910001563 bainite Inorganic materials 0.000 claims description 7
- 229910001562 pearlite Inorganic materials 0.000 claims description 7
- 239000012535 impurity Substances 0.000 claims description 4
- 238000005245 sintering Methods 0.000 description 32
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 23
- 239000011651 chromium Substances 0.000 description 21
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 21
- 239000000843 powder Substances 0.000 description 17
- 239000007791 liquid phase Substances 0.000 description 13
- 229910052751 metal Inorganic materials 0.000 description 11
- 239000002184 metal Substances 0.000 description 11
- 238000012360 testing method Methods 0.000 description 11
- 239000000463 material Substances 0.000 description 10
- 230000013011 mating Effects 0.000 description 10
- 239000000203 mixture Substances 0.000 description 10
- 229910045601 alloy Inorganic materials 0.000 description 7
- 239000000956 alloy Substances 0.000 description 7
- 150000001247 metal acetylides Chemical class 0.000 description 7
- 230000000052 comparative effect Effects 0.000 description 6
- 230000000704 physical effect Effects 0.000 description 6
- 238000002485 combustion reaction Methods 0.000 description 5
- 230000002159 abnormal effect Effects 0.000 description 4
- 238000005260 corrosion Methods 0.000 description 4
- 230000007797 corrosion Effects 0.000 description 4
- 229910052750 molybdenum Inorganic materials 0.000 description 4
- 229910052799 carbon Inorganic materials 0.000 description 3
- 229910052804 chromium Inorganic materials 0.000 description 3
- 238000001816 cooling Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 229910052759 nickel Inorganic materials 0.000 description 3
- 229910052698 phosphorus Inorganic materials 0.000 description 3
- 229910052710 silicon Inorganic materials 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 2
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 2
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 2
- 241000981595 Zoysia japonica Species 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 239000000314 lubricant Substances 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 239000011733 molybdenum Substances 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 239000011574 phosphorus Substances 0.000 description 2
- 239000011148 porous material Substances 0.000 description 2
- 239000010703 silicon Substances 0.000 description 2
- 239000013585 weight reducing agent Substances 0.000 description 2
- XOOUIPVCVHRTMJ-UHFFFAOYSA-L zinc stearate Chemical compound [Zn+2].CCCCCCCCCCCCCCCCCC([O-])=O.CCCCCCCCCCCCCCCCCC([O-])=O XOOUIPVCVHRTMJ-UHFFFAOYSA-L 0.000 description 2
- 229910000831 Steel Inorganic materials 0.000 description 1
- -1 T One or more of i Inorganic materials 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- 238000007710 freezing Methods 0.000 description 1
- 230000008014 freezing Effects 0.000 description 1
- 230000009191 jumping Effects 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 230000003578 releasing effect Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0264—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements the maximum content of each alloying element not exceeding 5%
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/009—Pearlite
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、内燃機関用摺動部
品として使用される焼結部材に関し、更に詳しくは、例
えば焼結カムシャフト用カムローブとして使用される耐
スカッフィング性および耐ピッチング性に優れた焼結部
材に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a sintered member used as a sliding part for an internal combustion engine, and more specifically, it has excellent scuffing resistance and pitting resistance used as a cam lobe for a sintered camshaft, for example. The present invention relates to a sintered member.
【０００２】[0002]
【従来の技術】内燃機関に使用される種々の摺動部品
は、高負荷運転に耐えることが要求され、特に摺動部品
の接触部分では高面圧に対する耐久性が要求されてい
る。こうした摺動部品は、軽量化、コスト低減、耐摩耗
性等の特性向上を目的として、焼結合金によって製造さ
れている。例えば、特公平３−６０９０１号公報には、
高硬度、高密度で耐摩耗性に優れた焼結合金が開示され
ている。2. Description of the Related Art Various sliding parts used in an internal combustion engine are required to withstand high load operation, and particularly, contact portions of the sliding parts are required to have durability against high surface pressure. Such sliding parts are made of a sintered alloy for the purpose of weight reduction, cost reduction, and improvement of properties such as wear resistance. For example, Japanese Patent Publication No. 3-60901 discloses that
A sintered alloy having high hardness, high density and excellent wear resistance is disclosed.
【０００３】このような焼結合金からなる焼結部材は、
例えばディーゼルエンジン部品であるカムシャフト用の
カムローブに使用された場合に、カムシャフトの軽量
化、コスト低減、耐摩耗性の向上等を達成することがで
きるので、好ましく使用されている。なお、このカムロ
ーブのように、相手材であるタペットとの間で滑りと転
がりが同時に起こる部材として使用される場合には、高
い耐スカッフィング性と耐ピッチング性（耐孔食性）が
要求される。A sintered member made of such a sintered alloy is
For example, when it is used in a cam lobe for a cam shaft which is a diesel engine component, it is possible to achieve weight reduction, cost reduction, improvement of wear resistance, etc. of the cam shaft, and therefore it is preferably used. When it is used as a member such as a cam lobe where sliding and rolling occur at the same time with a mating tappet, high scuffing resistance and high pitting resistance (pitting corrosion resistance) are required.
【０００４】[0004]
【発明が解決しようとする課題】従来のカムローブ等の
摺動部材には、焼入性が向上するように、すなわち冷却
速度が遅くてもマルテンサイト組織の生成を容易にさせ
て高い耐摩耗性を付与することができるように、Ｃｒ、
Ｍｏ、Ｎｉ等の元素を添加している。A conventional sliding member such as a cam lobe has a high wear resistance so that the hardenability is improved, that is, the martensite structure is easily generated even if the cooling rate is slow. , Cr,
Elements such as Mo and Ni are added.
【０００５】しかしながら、これらのＣｒ、Ｍｏ、Ｎｉ
等の元素は、焼結後の焼結部材の組織中に多くの残留オ
ーステナイトを残存させるため、焼結されたカムローブ
と滑りタイプのタペットとの間でスカッフが発生し、異
常摩耗が生じるおそれがあった。However, these Cr, Mo, Ni
Since elements such as leave a large amount of retained austenite in the structure of the sintered member after sintering, scuffing occurs between the sintered cam lobe and the sliding type tappet, and abnormal wear may occur. there were.
【０００６】こうした問題を解決するため、本発明は、
内燃機関用摺動部品として使用される耐スカッフィング
性と耐ピッチング性に優れた焼結部材、特に焼結カムシ
ャフト用カムローブとして使用される焼結部材を提供す
ることを目的とする。In order to solve these problems, the present invention provides
An object of the present invention is to provide a sintered member which is used as a sliding part for an internal combustion engine and has excellent scuffing resistance and pitting resistance, and particularly a sintered member which is used as a cam lobe for a sintered camshaft.
【０００７】[0007]
【課題を解決するための手段】本発明の第一の焼結部材
は、Ｃ：１．５〜３．０質量％、Ｃｒ：２．０〜１２．
０質量％、Ｍｏ：０．５〜３．０質量％、Ｓｉ：０．２
〜１．０質量％、Ｐ：０．２〜１．０質量％、残部Ｆｅ
および不可避不純物からなり、基地組織がパーライトで
あることに特徴を有する。この発明によれば、液相にお
いて焼結された焼結部材の合金基地が滑り性のよいパー
ライト組織であると共に、微細炭化物が多く析出するの
で、耐スカッフィング性に優れた焼結部材とすることが
できる。また、この焼結部材では、耐スカッフィング性
を低下させる残留オーステナイト量の残存が抑制され
る。The first sintered member of the present invention comprises C: 1.5 to 3.0 mass% and Cr: 2.0 to 12.
0 mass% , Mo: 0.5 to 3.0 mass% , Si: 0.2
~ 1.0 mass% , P: 0.2-1.0 mass% , balance Fe
And unavoidable impurities, and is characterized in that the matrix structure is pearlite. According to this invention, since the alloy matrix of the sintered member sintered in the liquid phase has a pearlite structure with good slipperiness and a large amount of fine carbide is precipitated, the sintered member has excellent scuffing resistance. You can In addition, in this sintered member, the residual austenite amount that reduces the scuffing resistance is suppressed from remaining.
【０００８】本発明の第二の焼結部材は、Ｃ：１．５〜
３．０質量％、Ｃｒ：２．０〜１２．０質量％、Ｍｏ：
０．５〜３．０質量％、Ｎｉ：１．４質量％以下、Ｓ
ｉ：０．２〜１．０質量％、Ｐ：０．２〜１．０質量
％、残部Ｆｅおよび不可避不純物からなり、基地組織
が、マルテンサイト、ベーナイトおよび残留オーステナ
イトの混在組織であることに特徴を有する。この発明に
よれば、焼結部材中のＮｉ含有量を１．４質量％以下の
範囲で調節することによって、スカッフの発生要因とな
る熱伝導性の悪い残留オーステナイト量を、異常摩耗等
の発生が起こらない範囲で調節することができる。さら
に、この焼結組織は、微細炭化物が多く析出したもので
あると共に、基地組織がマルテンサイト、ベーナイトお
よび残留オーステナイトの混在組織であるので、耐スカ
ッフィング性と耐ピッチング性に優れた焼結部材とする
ことができる。The second sintered member of the present invention has a C: 1.5-
3.0 mass% , Cr: 2.0 to 12.0 mass% , Mo:
0.5-3.0 mass% , Ni: 1.4 mass% or less, S
i: 0.2 to 1.0 mass% , P: 0.2 to 1.0 mass
% , The balance Fe and unavoidable impurities, and the matrix structure is a mixed structure of martensite, bainite, and retained austenite. According to the present invention, by adjusting the Ni content in the sintered member within the range of 1.4 % by mass or less, the amount of retained austenite having poor thermal conductivity, which causes scuffing, is reduced to cause abnormal wear. It can be adjusted within the range that does not occur. Further, this sintered structure is one in which a large amount of fine carbide is precipitated, and the matrix structure is a mixed structure of martensite, bainite and retained austenite, so that a sintered member excellent in scuffing resistance and pitting resistance is obtained. can do.
【０００９】前記残留オーステナイト量が、３０体積％
以下であることが好ましい。この発明によれば、残留オ
ーステナイト量が３０体積％以下であるので、特に滑り
タイプの焼結部材、例えばタペットを相手材とした部材
に好適に用いることができる。The amount of retained austenite is 30 % by volume.
The following is preferable. According to the present invention, since the amount of retained austenite is 30 % by volume or less, it can be suitably used particularly for a sliding type sintered member, for example, a member using a tappet as a mating member.
【００１０】上述の第一の焼結部材と第二の焼結部材の
ように、焼結部材の炭化物の大きさと基地組織を制御す
ることによって、相手材との滑り性等を改善することが
でき、耐スカッフィング性と耐ピッチング性を向上させ
ることができる。こうした基地組織が変化するのは、Ｎ
ｉ含有量を０〜１．４質量％の範囲内で適宜変化させる
ことによって材料の臨界冷却速度が変化することに依存
している。さらに、基地組織の変化は、同時に焼結部材
の硬さも変化させるので、相手材に応じた特性を有する
焼結部材を得ることができる。Like the above-mentioned first sintered member and second sintered member, by controlling the size of the carbide and the matrix structure of the sintered member, it is possible to improve the slidability with the mating member. It is possible to improve scuffing resistance and pitting resistance. It is N
It depends on the change of the critical cooling rate of the material by appropriately changing the i content within the range of 0 to 1.4 mass% . Further, since the hardness of the sintered member changes at the same time when the matrix structure changes, it is possible to obtain a sintered member having characteristics according to the mating material.
【００１１】前記の焼結部材が、焼結カムシャフト用カ
ムローブであることが好ましい。この発明によれば、耐
スカッフィング性および耐ピッチング性に優れたカムシ
ャフト用カムローブを得ることができる。また、上記の
ように、Ｎｉ含有量を所定の範囲で変化させることによ
って、得られたカムローブの硬さを調節することが可能
となり、相手材であるタペット等の材質に応じた特性を
有するカムローブを得ることができるので、相手材との
組み合わせ範囲を広くすることができる。The sintered member is preferably a cam lobe for a sintered cam shaft. According to the present invention, a cam lobe for a camshaft having excellent scuffing resistance and pitching resistance can be obtained. Further, as described above, by changing the Ni content within a predetermined range, it becomes possible to adjust the hardness of the obtained cam lobe, and the cam lobe having characteristics according to the material of the mating material such as tappet. Therefore, the range of combination with the mating material can be widened.
【００１２】[0012]
【発明の実施の形態】次に、本発明の第一の焼結部材お
よび第二の焼結部材について説明する。BEST MODE FOR CARRYING OUT THE INVENTION Next, the first sintered member and the second sintered member of the present invention will be described.
【００１３】先ず、本発明の第一の焼結部材は、焼結用
粉末として、主要成分となる鉄粉または所定の元素を含
んだ鉄系合金粉末中に、焼結後の成分組成がＣ（炭
素）：１．５〜３．０質量％、Ｃｒ（クロム）：２．０
〜１２．０質量％、Ｍｏ（モリブデン）：０．５〜３．
０質量％、Ｓｉ（珪素）０．２〜１．０質量％、Ｐ（リ
ン）０．２〜１．０質量％となるように所定量を添加
し、焼結用粉末を調製する。次いで、通常の焼結方法に
より、焼結用粉末をプレス成形して圧粉体を形成し、液
相において焼結処理することにより本発明の焼結部材を
製造する。First, in the first sintered member of the present invention, as a sintering powder, iron powder as a main component or iron-based alloy powder containing a predetermined element has a component composition of C after sintering. (Carbon): 1.5 to 3.0 mass% , Cr (chromium): 2.0
~ 12.0 mass% , Mo (molybdenum): 0.5-3.
0 % by mass , Si (silicon) 0.2 to 1.0 % by mass , and P (phosphorus) 0.2 to 1.0 % by mass are added in predetermined amounts to prepare a sintering powder. Then, by a normal sintering method, the sintering powder is press-molded to form a green compact, which is then sintered in the liquid phase to produce the sintered member of the present invention.
【００１４】得られた焼結部材は、その基地組織が滑り
性のよいパーライト組織となるので、マルテンサイト基
地を伴う従来の焼結部材に比べて滑り性が向上し、耐ス
カッフィング性を向上させると共に、微細炭化物が多く
析出するので耐摩耗性も向上する。また、上記組成の焼
結部材には、耐スカッフィング性を低下させる残留オー
ステナイトがあまり残存しないので、残留オーステナイ
トを要因とした耐スカッフィング性の低下を抑制するこ
とができる。Since the matrix structure of the obtained sintered member is a pearlite structure having a good slip property, the slip property is improved and the scuffing resistance is improved as compared with the conventional sintered member having a martensite matrix. At the same time, since a large amount of fine carbide is precipitated, wear resistance is also improved. Further, since the retained austenite that reduces the scuffing resistance does not remain so much in the sintered member having the above composition, it is possible to suppress the reduction in the scuffing resistance due to the retained austenite.
【００１５】次に、本発明の第二の焼結部材について説
明する。本発明の第二の焼結部材は、Ｎｉが添加された
成分組成となるほかは、上述の第一の焼結部材と同様の
方法で製造される。すなわち、第一の焼結部材は、主要
成分となる鉄粉または所定の元素を含んだ鉄系合金粉末
中に、焼結後の成分組成がＣ（炭素）：１．５〜３．０
質量％、Ｃｒ（クロム）：２．０〜１２．０質量％、Ｍ
ｏ（モリブデン）：０．５〜３．０質量％、Ｎｉ（ニッ
ケル）：１．４質量％以下、Ｓｉ（珪素）０．２〜１．
０質量％、Ｐ（リン）０．２〜１．０質量％となるよう
に所定量を添加し、焼結用粉末を調製したものである。Next, the second sintered member of the present invention will be described. The second sintered member of the present invention is manufactured by the same method as that of the above-mentioned first sintered member except that it has a component composition to which Ni is added. That is, in the first sintered member, the component composition after sintering is C (carbon): 1.5 to 3.0 in the iron powder as the main component or the iron-based alloy powder containing the predetermined element.
% By mass , Cr (chrome): 2.0 to 12.0 % by mass , M
o (molybdenum): 0.5 to 3.0 mass% , Ni (nickel): 1.4 mass% or less, Si (silicon) 0.2 to 1.
A predetermined amount was added so that 0 % by mass and 0.2 to 1.0 % by mass of P (phosphorus) were added to prepare a powder for sintering.
【００１６】得られた焼結部材は、スカッフの発生要因
となる熱伝導性の悪い残留オーステナイト量が、異常摩
耗等の発生が起こらない範囲に調節されている。さら
に、この焼結組織は、微細炭化物が多く析出すると共
に、基地組織がマルテンサイト、ベーナイトおよび残留
オーステナイトの混在組織であるので、耐スカッフィン
グ性と耐ピッチング性に優れた焼結部材とすることがで
きる。In the obtained sintered member, the amount of retained austenite having poor thermal conductivity, which causes scuffing, is adjusted within a range where abnormal wear or the like does not occur. Furthermore, this sintered structure has a large amount of fine carbide precipitated, and since the matrix structure is a mixed structure of martensite, bainite and retained austenite, it can be a sintered member having excellent scuffing resistance and pitting resistance. it can.
【００１７】Ｎｉは、基地強化の目的で添加され、焼結
後の基地組織をマルテンサイト化して引張り強度を増大
させることができる。焼結部材中のＮｉ量は、スカッフ
の発生要因となる基地中の残留オーステナイト量を調節
して、耐スカッフィング性を維持するため、１．４質量
％以下とした。Ni is added for the purpose of strengthening the matrix, and the matrix structure after sintering can be converted to martensite to increase the tensile strength. The amount of Ni in the sintered member is 1.4% by mass in order to maintain the scuffing resistance by adjusting the amount of retained austenite in the matrix that causes scuffing.
% Or less.
【００１８】図１は、焼結部材中のＮｉ含有量（質量
％）と、基地中の残留オーステナイト組織の割合（体積
％）および硬さ（ＨＲＣ）との関係を示すグラフであ
る。図１に示すように、Ｎｉ含有量が１．４質量％を超
えると、基地中の残留オーステナイト量が３０体積％を
超える。残留オーステナイト量が３０体積％を超えた焼
結部材は、スカッフの発生するおそれが認められる。基
地中の残留オーステナイトは、耐摩耗性を向上させるに
は好ましい場合があるが、耐スカッフィング性に対して
は好ましくない。従って、良好な耐スカッフィング性を
得るためには、基地中の残留オーステナイト組織の割合
を３０体積％以下にすることが好ましい。また、図１に
示すように、Ｎｉ含有量が１．４質量％以下のときの焼
結部材の最高硬さは、ＨＲＣ６２程度であるが、Ｎｉ含
有量が１．４質量％を超えても硬さはほとんど変化する
ことはない。そのため、Ｎｉ含有量を１．４質量％以下
に限定する。得られた焼結部材は、パーライト、マルテ
ンサイトおよび残留オーステナイトとの混在組織からな
り、高強度で、耐スカッフィング性および耐ピッチング
性に優れている。FIG. 1 shows the Ni content ( mass ) of the sintered member.
% ) And the proportion of retained austenite structure in the matrix ( volume
% ) And hardness (HRC). As shown in FIG. 1, when the Ni content exceeds 1.4 % by mass , the amount of retained austenite in the matrix exceeds 30 % by volume . It is recognized that scuffing may occur in a sintered member having a residual austenite amount exceeding 30 % by volume . Retained austenite in the matrix may be preferable for improving wear resistance, but it is not preferable for scuffing resistance. Therefore, in order to obtain good scuffing resistance, the proportion of the retained austenite structure in the matrix is preferably 30 % by volume or less. Further, as shown in FIG. 1, the maximum hardness of the sintered member when the Ni content is 1.4 mass% or less is about HRC62, but even when the Ni content exceeds 1.4 mass%. Hardness hardly changes. Therefore, the Ni content is limited to 1.4 % by mass or less. The obtained sintered member has a mixed structure of pearlite, martensite, and retained austenite, has high strength, and is excellent in scuffing resistance and pitting resistance.
【００１９】次に、他の成分元素を上述の範囲に限定し
た理由について説明する。Next, the reason why the other constituent elements are limited to the above range will be described.
【００２０】Ｃ含有量が３．０質量％を超えると、粗大
な炭化物、特に粗大なＣｒ炭化物が焼結部材中で形成さ
れる。この粗大な炭化物は、液相焼結中に粗大な空孔を
生じさせて、基地を脆化させる。また、Ｃ含有量が１．
５質量％未満では、高硬度の微細炭化物が十分に形成さ
れず、十分な耐摩耗性および耐スカッフィング性を満た
すには十分でない。このため、Ｃ含有量を１．５〜３．
０質量％に限定する。また、得られる焼結部材を、高負
荷、高面圧の内燃機関の摺動部材として用いる場合に
は、Ｃｒ含有量を６．０〜１２．０質量％と高めにする
と共に、Ｃ含有量も２．０〜３．０質量％と高めにする
ことがより好ましい。If the C content exceeds 3.0 % by mass , coarse carbides, especially coarse Cr carbides are formed in the sintered member. This coarse carbide causes coarse pores during liquid phase sintering to embrittle the matrix. Further, the C content is 1.
If it is less than 5 % by mass , fine carbide having high hardness is not sufficiently formed, and it is not sufficient to satisfy sufficient wear resistance and scuffing resistance. Therefore, the C content is 1.5 to 3.
It is limited to 0 % by mass . When the obtained sintered member is used as a sliding member for an internal combustion engine having a high load and a high surface pressure, the Cr content is increased to 6.0 to 12.0 mass% and the C content is increased. It is more preferable to set the content to a high value of 2.0 to 3.0 % by mass .
【００２１】Ｃｒ含有量が１２．０質量％を超えると、
Ｃｒ炭化物を微細化させる度合いが小さくなり、硬さも
過大になる。Ｃｒ含有量が２．０質量％未満では、Ｃｒ
炭化物がやや粗大になってくるので、高硬度の微細炭化
物を十分に形成することができず、十分な耐摩耗性およ
び耐スカッフィング性を満足することができない。この
ため、Ｃｒ含有量を２．０〜１２．０質量％に限定す
る。また、高負荷、高面圧の内燃機関の摺動部材として
用いる場合には、Ｃ含有量との関係において、上述の範
囲とすることが好ましい。When the Cr content exceeds 12.0 mass% ,
The degree of refining the Cr carbide becomes small and the hardness becomes excessive. If the Cr content is less than 2.0 % by mass , Cr
Since the carbides become a little coarse, it is not possible to sufficiently form high hardness fine carbides, and it is not possible to satisfy sufficient wear resistance and scuffing resistance. Therefore, the Cr content is limited to 2.0 to 12.0 mass% . Further, when it is used as a sliding member of an internal combustion engine having a high load and a high surface pressure, the above range is preferable in relation to the C content.
【００２２】Ｍｏは基地に固溶して硬度を高め、耐摩耗
性を向上させる。しかし、この効果は、Ｍｏ含有量が
３．０質量％を超えてもほとんど変化しない。また、Ｍ
ｏ含有量が０．５質量％未満では、こうした効果を十分
に得ることができない。このため、Ｍｏ含有量を０．５
〜３．０質量％に限定する。なお、この範囲内のＭｏ
は、残留オーステナイト量に影響を及ぼさない。Mo forms a solid solution in the matrix to increase hardness and improve wear resistance. However, this effect hardly changes even when the Mo content exceeds 3.0 mass% . Also, M
If the o content is less than 0.5 % by mass , such effects cannot be sufficiently obtained. Therefore, the Mo content is 0.5
To 3.0 % by mass . In addition, Mo within this range
Does not affect the amount of retained austenite.
【００２３】Ｓｉ含有量が１．０質量％を超えると、基
地が脆化するほか、粉末の圧粉成形性が低下し、焼結後
の焼結部材の変形が大きくなる。また、Ｓｉは、Ｃおよ
びＰ含有量を低くした際に液相の生成を促進させる成分
であるが、Ｓｉ含有量が０．２質量％未満では液相促進
の効果が得られない。このため、Ｓｉ含有量を０．２〜
１．０質量％に限定する。When the Si content exceeds 1.0 % by mass , the matrix becomes brittle, and the powder compactability of the powder deteriorates, resulting in large deformation of the sintered member after sintering. Further, Si is a component that promotes the generation of the liquid phase when the C and P contents are lowered, but if the Si content is less than 0.2 mass% , the effect of promoting the liquid phase cannot be obtained. Therefore, the Si content is 0.2 to
It is limited to 1.0 % by mass .
【００２４】ＰはＦｅ−Ｃ−Ｐ共晶のステダイトを生じ
させる。ステダイトは硬度が非常に高く、凝固点が９５
０℃前後と低いため液相焼結を促進させる。しかし、Ｐ
含有量が１．０質量％を超えると、ステダイトが過多に
生じ、被削性が悪くなる。また、０．２質量％未満で
は、ステダイトの析出量が少なくなって、高い耐摩耗性
が得られず、また、液相も生じにくくなる。このため、
Ｐ含有量を０．２〜１．０質量％に限定する。P produces a Fe-C-P eutectic steadite. Steadite has a very high hardness and a freezing point of 95.
Since it is as low as around 0 ° C, it promotes liquid phase sintering. But P
If the content exceeds 1.0 % by mass , excessive studite is generated, resulting in poor machinability. On the other hand, if it is less than 0.2 % by mass , the precipitation amount of steadite will be small, high abrasion resistance will not be obtained, and the liquid phase will not easily occur. For this reason,
The P content is limited to 0.2 to 1.0 % by mass .
【００２５】その他の粉末としては、Ｍｎ、Ｂ、Ｖ、Ｔ
ｉ、Ｎｂ、Ｗの中の一種類以上を必要に応じて添加する
ことができる。例えば、１．０質量％以下のＭｎを添加
することができる。Ｍｎ含有量が１．０質量％を超える
と、焼結の進行が抑制されるため、粗大な空孔が残って
圧粉成形性が低下する。また、他の元素を添加する目的
は、液相の成長と炭化物の形成を促進させることにある
が、添加量は相手材の硬度を考慮して０．１〜５．０質
量％の範囲内で適宜適量を添加することが望ましい。さ
らに、加工性を改善するために、３００ｐｐｍ以下のＣ
ａを添加することもできる。Other powders include Mn, B, V, T
One or more of i, Nb, and W can be added if necessary. For example, 1.0 % by mass or less of Mn can be added. If the Mn content exceeds 1.0 % by mass , the progress of sintering is suppressed, so that coarse pores remain and the powder compactability is reduced. Moreover, the purpose of adding other elements is to promote the growth of the liquid phase and the formation of carbides, but the addition amount is 0.1 to 5.0 in consideration of the hardness of the mating material.
It is desirable to add an appropriate amount within the range of the amount% . Furthermore, in order to improve workability, C of 300 ppm or less is used.
It is also possible to add a.
【００２６】こうして調製された焼結用粉末には、金型
成型時の型抜け性を良くするために、例えばステアリン
酸亜鉛等の潤滑剤が添加される。A lubricant such as zinc stearate, for example, is added to the powder for sintering thus prepared in order to improve the mold releasing property at the time of mold molding.
【００２７】液相において焼結処理するための好ましい
温度は１１００〜１２００℃であり、更に好ましくは１
１１０〜１１６０℃である。また、この時の焼結時間は
６０〜９０分間程度が好ましい。また、必要に応じて焼
き戻し処理等を行い、得られる焼結部材の特性を調整す
ることもできる。The preferable temperature for the sintering treatment in the liquid phase is 1100 to 1200 ° C., more preferably 1
It is 110-1160 degreeC. The sintering time at this time is preferably about 60 to 90 minutes. Further, if necessary, tempering treatment or the like can be performed to adjust the characteristics of the obtained sintered member.
【００２８】本発明の焼結部材は、カムローブ材等の摺
動部材としての使用を主目的としているので、通常、液
相焼結される。その結果、液相焼結時の収縮によって、
母材に対して強固に固着させることができる。例えば、
シャフトを鋼管とし、このシャフトに焼結部材であるカ
ムローブを組み付ける構造のカムシャフトの場合、液相
焼結により、シャフトに強固に拡散接合させた高密度の
カムローブを得ることができる。こうして得られた焼結
部材は、耐スカッフィング性および耐摩耗性において優
れた特性を有し、さらに、加工性とコストパフォーマン
スにおいても優れている。Since the sintered member of the present invention is mainly intended for use as a sliding member such as a cam lobe material, it is usually liquid phase sintered. As a result, due to shrinkage during liquid phase sintering,
It can be firmly fixed to the base material. For example,
In the case of a camshaft having a structure in which the shaft is a steel pipe and a cam lobe that is a sintered member is assembled to the shaft, liquid phase sintering can provide a high-density cam lobe that is firmly diffusion bonded to the shaft. The sintered member thus obtained has excellent properties in scuffing resistance and wear resistance, and is also excellent in workability and cost performance.
【００２９】[0029]
【実施例】次に、本発明の焼結部材を、実施例および比
較例によって、更に具体的に説明する。EXAMPLES Next, the sintered member of the present invention will be described more specifically by way of Examples and Comparative Examples.
【００３０】（実施例１）
焼結後の成分組成が、Ｃ：２．０質量％、Ｃｒ：４．０
質量％、Ｍｏ：１．０質量％、Ｓｉ：０．８質量％、
Ｐ：０．５質量％、Ｆｅ：残り、となるように、各元素
を鉄粉中に添加して焼結用粉末を調整した。さらに、潤
滑剤としてステアリン酸亜鉛を加えて混合した。次い
で、５〜７ｔ／ｃｍ2 の面圧でプレス成形して圧粉体を
形成した後、真空焼結炉中で、１１００〜１２００℃
（平均１１６０℃）の温度で焼結し、実施例１の焼結部
材を得た。Example 1 The composition of components after sintering was C: 2.0 % by mass , Cr: 4.0.
% By mass , Mo: 1.0 % by mass , Si: 0.8 % by mass ,
Powders for sintering were prepared by adding the respective elements to the iron powder so that P: 0.5 % by mass and Fe: balance. Furthermore, zinc stearate was added as a lubricant and mixed. Next, after press forming with a surface pressure of 5 to 7 t / cm 2 to form a green compact, it is 1100 to 1200 ° C. in a vacuum sintering furnace.
Sintering was performed at a temperature of (average 1160 ° C.) to obtain a sintered member of Example 1.
【００３１】物性等の試験結果を表１に示した。金属組
織の顕微鏡写真（２００倍、ナイタル腐食）を図２に示
し、この金属組織の模式的な説明図を図３に示した。Table 1 shows the test results of physical properties and the like. A photomicrograph (200 times, nital corrosion) of the metal structure is shown in FIG. 2, and a schematic explanatory view of this metal structure is shown in FIG.
【００３２】（実施例２）
焼結後の成分組成が、Ｃ：２．６質量％、Ｃｒ：８．０
質量％、Ｍｏ：２．０質量％、Ｎｉ：１．０質量％、Ｓ
ｉ：０．８質量％、Ｐ：０．５質量％、Ｆｅ：残り、と
なるように、各元素を鉄粉中に添加して焼結用粉末を調
整した。その他は、実施例１と同様として、実施例２の
焼結部材を得た。Example 2 The composition of components after sintering was C: 2.6 % by mass , Cr: 8.0.
% By mass , Mo: 2.0 % by mass , Ni: 1.0 % by mass , S
Each element was added to the iron powder to prepare a sintering powder such that i: 0.8 % by mass , P: 0.5 % by mass , and Fe: rest. Others were the same as that of Example 1, and the sintered member of Example 2 was obtained.
【００３３】物性等の試験結果を表１に示した。金属組
織の顕微鏡写真（２００倍、ナイタル腐食）を図４に示
し、この金属組織の模式的な説明図を図５に示した。The test results of the physical properties are shown in Table 1. A photomicrograph (200 times, nital corrosion) of the metal structure is shown in FIG. 4, and a schematic explanatory view of this metal structure is shown in FIG.
【００３４】（実施例３）
焼結後の成分組成が、Ｃ：２．０質量％、Ｃｒ：４．０
質量％、Ｍｏ：１．０質量％、Ｎｉ：１．３質量％、Ｓ
ｉ：０．８質量％、Ｐ：０．５質量％、Ｆｅ：残り、と
なるように、各元素を鉄粉中に添加して焼結用粉末を調
整した。その他は、実施例１と同様として、実施例３の
焼結部材を得た。(Example 3) The composition of components after sintering was C: 2.0 % by mass , Cr: 4.0.
% By mass , Mo: 1.0 % by mass , Ni: 1.3 % by mass , S
Each element was added to the iron powder to prepare a sintering powder such that i: 0.8 % by mass , P: 0.5 % by mass , and Fe: rest. Others were the same as that of Example 1, and the sintered member of Example 3 was obtained.
【００３５】物性等の試験結果を表１に示した。金属組
織の顕微鏡写真（２００倍、ナイタル腐食）を図６に示
し、この金属組織の模式的な説明図を図７に示した。Table 1 shows the test results of physical properties and the like. A photomicrograph (200 times, nital corrosion) of the metal structure is shown in FIG. 6, and a schematic explanatory view of this metal structure is shown in FIG.
【００３６】（実施例４）
焼結後の成分組成が、Ｃ：２．４質量％、Ｃｒ：１２．
０質量％、Ｍｏ：１．０質量％、Ｓｉ：０．８質量％、
Ｐ：０．５質量％、Ｆｅ：残り、となるように、各元素
を鉄粉中に添加して焼結用粉末を調整した。その他は、
実施例１と同様として、実施例４の焼結部材を得た。物
性等の試験結果を表１に示した。(Example 4) The composition of components after sintering was C: 2.4 mass% , Cr: 12.
0 mass% , Mo: 1.0 mass% , Si: 0.8 mass% ,
Powders for sintering were prepared by adding the respective elements to the iron powder so that P: 0.5 % by mass and Fe: balance. Others
A sintered member of Example 4 was obtained in the same manner as in Example 1. The test results of physical properties are shown in Table 1.
【００３７】（比較例１）
焼結後の成分組成が、Ｃ：２．６質量％、Ｃｒ：８．０
質量％、Ｍｏ：１．０質量％、Ｎｉ：２．０質量％、Ｓ
ｉ：０．８質量％、Ｐ：０．５質量％、Ｆｅ：残り、と
なるように、各元素を鉄粉中に添加して焼結用粉末を調
整した。その他は、実施例１と同様として、比較例１の
焼結部材を得た。物性等の試験結果を表１に示した。Comparative Example 1 The composition of components after sintering was C: 2.6 % by mass , Cr: 8.0.
% By mass , Mo: 1.0 % by mass , Ni: 2.0 % by mass , S
Each element was added to the iron powder to prepare a sintering powder such that i: 0.8 % by mass , P: 0.5 % by mass , and Fe: rest. Others were the same as that of Example 1, and the sintered member of the comparative example 1 was obtained. The test results of physical properties are shown in Table 1.
【００３８】（比較例２）
焼結後の成分組成が、Ｃ：２．８質量％、Ｃｒ：１５．
５質量％、Ｍｏ：１．０質量％、Ｎｉ：１．９質量％、
Ｓｉ：０．９質量％、Ｐ：０．５質量％、Ｖ：３．５質
量％、Ｆｅ：残り、となるように、各元素を鉄粉中に添
加して焼結用粉末を調整した。その他は、実施例１と同
様として、比較例２の焼結部材を得た。物性等の試験結
果を表１に示した。Comparative Example 2 The composition of components after sintering was C: 2.8 mass% , Cr: 15.
5 % by mass , Mo: 1.0 % by mass , Ni: 1.9 % by mass ,
Si: 0.9 mass% , P: 0.5 mass% , V: 3.5 quality
Powders for sintering were prepared by adding the respective elements to the iron powder so that the amount of Fe was: % and the balance was Fe. Others were the same as that of Example 1, and the sintered member of the comparative example 2 was obtained. The test results of physical properties are shown in Table 1.
【００３９】（試験及び結果）
耐スカッフィング性は、バルブスプリング力を実機エン
ジンよりも増大させてモータリング試験を実施し、試験
後のカムシャフトカムローブ部を観察することによって
評価した。(Tests and Results) The scuffing resistance was evaluated by performing a motoring test with the valve spring force increased from that of an actual engine and observing the camshaft cam lobe portion after the test.
【００４０】耐ピッチング性は、実機エンジンにて、タ
ペットのジャンピングが発生する高回転域を多用し、カ
ムノーズ部付近のカム／タペット間の接触面圧を過酷に
した条件でのファイアリング試験を実施し、試験後のカ
ムシャフトカムローブ部を観察することによって評価し
た。For the anti-pitting property, in the actual engine, the firing test was conducted under the condition that the contact surface pressure between the cam and the tappet near the cam nose part was severely used by frequently using the high rotation range where the tappet jumping occurs. Then, the evaluation was made by observing the camshaft cam lobe portion after the test.
【００４１】なお、焼結部材のロックウェル硬さ（ＨＲ
Ｃ）は従来通りの方法で測定し、炭化物の大きさは拡大
写真から測定し、残留オーステナイト量の測定はＸ線
（定量）測定により行った。The Rockwell hardness of the sintered member (HR
C) was measured by a conventional method, the size of the carbide was measured from an enlarged photograph, and the amount of retained austenite was measured by X-ray (quantitative) measurement.
【００４２】[0042]
【表１】 [Table 1]
【００４３】焼結部材の組織としては、本発明の第一の
焼結部材は、図２及び図３に示すように、基地組織が滑
り性のよいパーライトからなり、炭化物が粒子状に分布
していた。また、本発明の第二の焼結部材は、図４〜図
７に示すように、基地組織がマルテンサイト、ベイナイ
トおよび残留オーステナイトの混在組織であり、白く見
える炭化物が粒子状に分布していた。これらは何れも残
留オーステナイトは３０体積％以下であり、この範囲で
好ましい耐スカッフィング性および耐ピッチング性等を
示した。As for the structure of the sintered member, in the first sintered member of the present invention, as shown in FIGS. 2 and 3, the matrix structure is made of pearlite having good slipperiness, and the carbide is distributed in particles. Was there. Further, in the second sintered member of the present invention, as shown in FIGS. 4 to 7, the matrix structure was a mixed structure of martensite, bainite and retained austenite, and white-looking carbides were distributed in particles. . The residual austenite content was 30 % by volume or less in all of these, and preferred scuffing resistance and pitting resistance were exhibited in this range.
【００４４】これに対して、比較例１および比較例２で
得られた焼結部材は、本発明の第二の焼結部材と同様
に、基地組織がマルテンサイト、ベイナイトおよび残留
オーステナイトの混在組織であったが、これらのうち残
留オーステナイト組織の割合が何れも３０体積％を超え
ており、スカッフィングの発生によりピッチングが発生
する結果となった。On the other hand, in the sintered members obtained in Comparative Examples 1 and 2, the matrix structure is a mixed structure of martensite, bainite and retained austenite, as in the second sintered member of the present invention. However, the proportion of the retained austenite structure in each of these exceeded 30 % by volume , resulting in the occurrence of pitching due to the occurrence of scuffing.
【００４５】従って、耐スカッフィング性等の特性を向
上させるためには、Ｎｉを含まないか、含むとすれば
１．４質量％以下にする必要があることがわかる。Therefore, in order to improve the properties such as scuffing resistance, it should be understood that Ni is not included, or if it is included, it must be 1.4 mass% or less.
【００４６】[0046]
【発明の効果】以上述べたように、本発明の第一の焼結
部材によれば、液相において焼結された焼結部材の合金
基地が滑り性のよいパーライト組織であると共に、微細
炭化物が多く析出するので、耐スカッフィング性に優れ
た焼結部材とすることができる。また、この焼結部材で
は、耐スカッフィング性を低下させる残留オーステナイ
ト量の残存が抑制される。As described above, according to the first sintered member of the present invention, the alloy base of the sintered member sintered in the liquid phase has a pearlite structure with good slipperiness and fine carbides. Since a large amount is deposited, a sintered member having excellent scuffing resistance can be obtained. In addition, in this sintered member, the residual austenite amount that reduces the scuffing resistance is suppressed from remaining.
【００４７】また、本発明の第二の焼結部材によれば、
焼結部材中のＮｉ含有量を１．４質量％以下の範囲で調
節することによって、スカッフの発生要因となる熱伝導
性の悪い残留オーステナイト量を、異常摩耗等の発生が
起こらない範囲で調節することができる。さらに、この
焼結組織は、微細炭化物が多く析出したものであると共
に、基地組織がマルテンサイト、ベーナイトおよび残留
オーステナイトの混在組織であるので、耐スカッフィン
グ性と耐ピッチング性に優れた焼結部材とすることがで
きる。このとき、残留オーステナイト量を３０体積％以
下とすることにより、特に滑りタイプの焼結部材、例え
ばタペットを相手材とした部材に好適に用いることがで
きる。According to the second sintered member of the present invention,
By adjusting the Ni content in the sintered member within the range of 1.4 mass% or less, the amount of retained austenite with poor thermal conductivity that causes scuffing can be adjusted within the range where abnormal wear does not occur. can do. Further, this sintered structure is one in which a large amount of fine carbide is precipitated, and the matrix structure is a mixed structure of martensite, bainite and retained austenite, so that a sintered member excellent in scuffing resistance and pitting resistance is obtained. can do. At this time, when the amount of retained austenite is 30 % by volume or less, it can be suitably used particularly for a sliding type sintered member, for example, a member using tappet as a mating member.
【００４８】上記の第一の焼結部材と第二の焼結部材の
ように、焼結部材の炭化物の大きさと基地組織を制御す
ることによって、相手材との滑り性等を改善することが
でき、耐スカッフィング性と耐ピッチング性を向上させ
ることができる。こうした基地組織が変化するのは、Ｎ
ｉ含有量を０〜１．４質量％の範囲内で適宜変化させる
ことによって材料の臨界冷却速度が変化することに依存
している。さらに、基地組織の変化は、同時に焼結部材
の硬さも変化させるので、相手材に応じた特性を有する
焼結部材、特に焼結カムシャフト用カムローブを得るこ
とができる。Like the above-mentioned first sintered member and second sintered member, by controlling the size of the carbide and the matrix structure of the sintered member, it is possible to improve the slidability with the mating member. It is possible to improve scuffing resistance and pitting resistance. It is N
It depends on the change of the critical cooling rate of the material by appropriately changing the i content within the range of 0 to 1.4 mass% . Furthermore, since the hardness of the sintered member changes at the same time when the matrix structure changes, it is possible to obtain a sintered member, especially a cam lobe for a sintered camshaft, which has characteristics according to the mating material.
【図１】焼結部材中のＮｉ含有量（質量％）と、基地中
の残留オーステナイト組織の割合（体積％）および硬さ
（ＨＲＣ）との関係を示すグラフである。FIG. 1 is a graph showing a relationship between a Ni content ( mass% ) in a sintered member, a proportion ( volume% ) of a retained austenite structure in a matrix, and a hardness (HRC).
【図２】実施例１で得られた焼結部材の金属組織を示す
図面代用写真である。2 is a drawing-substituting photograph showing the metallographic structure of the sintered member obtained in Example 1. FIG.
【図３】図２の金属組織の模式的な説明図である。FIG. 3 is a schematic explanatory view of the metal structure of FIG.
【図４】実施例２で得られた焼結部材の金属組織を示す
図面代用写真である。4 is a drawing-substituting photograph showing the metal structure of the sintered member obtained in Example 2. FIG.
【図５】図４の金属組織の模式的な説明図である。5 is a schematic explanatory view of the metal structure of FIG. 4. FIG.
【図６】実施例３で得られた焼結部材の金属組織を示す
図面代用写真である。FIG. 6 is a drawing-substituting photograph showing the metal structure of the sintered member obtained in Example 3.
【図７】図６の金属組織の模式的な説明図である。FIG. 7 is a schematic explanatory view of the metal structure of FIG.
１ 基地 ２ Ｃｒ炭化物 ３ 複合炭化物 1 base 2 Cr carbide 3 composite carbide
───────────────────────────────────────────────────── フロントページの続き (72)発明者 宮内 憲一 東京都港区芝五丁目33番８号 三菱自動 車工業株式会社内 (72)発明者 小林 幹和 東京都港区芝五丁目33番８号 三菱自動 車工業株式会社内 (56)参考文献 特開 昭60−33344（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) C22C 38/00 B22F 1/00 F01L 1/04 ─────────────────────────────────────────────────── ─── Continuation of front page (72) Inventor Kenichi Miyauchi 5-3-8 Shiba, Minato-ku, Tokyo Mitsubishi Motors Corporation (72) Inventor Mikikazu Kobayashi 5-3-8 Shiba, Minato-ku, Tokyo No. Mitsubishi Motors Corporation (56) Reference JP-A-60-33344 (JP, A) (58) Fields investigated (Int.Cl. 7 , DB name) C22C 38/00 B22F 1/00 F01L 1 / 04
Claims (4)
０〜１２．０質量％、Ｍｏ：０．５〜３．０質量％、Ｓ
ｉ：０．２〜１．０質量％、Ｐ：０．２〜１．０質量
％、残部Ｆｅおよび不可避不純物からなり、基地組織が
パーライトであることを特徴とする焼結部材。1. C: 1.5 to 3.0 % by mass , Cr: 2.
0 to 12.0 mass% , Mo: 0.5 to 3.0 mass% , S
i: 0.2 to 1.0 mass% , P: 0.2 to 1.0 mass
% , The balance Fe, and unavoidable impurities, and the matrix structure is pearlite.
０〜１２．０質量％、Ｍｏ：０．５〜３．０質量％、Ｎ
ｉ：１．４質量％以下、Ｓｉ：０．２〜１．０質量％、
Ｐ：０．２〜１．０質量％、残部Ｆｅおよび不可避不純
物からなり、基地組織が、マルテンサイト、ベーナイト
および残留オーステナイトの混在組織であることを特徴
とする焼結部材。2. C: 1.5 to 3.0 % by mass , Cr: 2.
0 to 12.0 mass% , Mo: 0.5 to 3.0 mass% , N
i: 1.4 % by mass or less, Si: 0.2 to 1.0 % by mass ,
P: 0.2 to 1.0 % by mass , the balance being Fe and unavoidable impurities, and the matrix structure is a mixed structure of martensite, bainite, and retained austenite.
％以下であることを特徴とする請求項２に記載の焼結部
材。3. The amount of retained austenite is 30 volumes
% Or less, The sintered member according to claim 2.
カムローブであることを特徴とする請求項１乃至請求項
３の何れかに記載の焼結部材。4. The sintered member according to any one of claims 1 to 3, wherein the sintered member is a cam lobe for a sintered cam shaft.
Priority Applications (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP34654198A JP3440008B2 (en) | 1998-11-18 | 1998-11-18 | Sintered member |
| KR10-1999-0050406A KR100409137B1 (en) | 1998-11-18 | 1999-11-13 | Sintered member |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP34654198A JP3440008B2 (en) | 1998-11-18 | 1998-11-18 | Sintered member |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2000144341A JP2000144341A (en) | 2000-05-26 |
| JP3440008B2 true JP3440008B2 (en) | 2003-08-25 |
Family
ID=18384130
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP34654198A Expired - Fee Related JP3440008B2 (en) | 1998-11-18 | 1998-11-18 | Sintered member |
Country Status (2)
| Country | Link |
|---|---|
| JP (1) | JP3440008B2 (en) |
| KR (1) | KR100409137B1 (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP3777079B2 (en) * | 2000-02-17 | 2006-05-24 | 日本ピストンリング株式会社 | Camshaft |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6033344A (en) * | 1983-08-03 | 1985-02-20 | Nippon Piston Ring Co Ltd | Wear resistance sintered alloy |
| JP2733773B2 (en) * | 1988-08-30 | 1998-03-30 | 日本ピストンリング株式会社 | Rocker arm |
-
1998
- 1998-11-18 JP JP34654198A patent/JP3440008B2/en not_active Expired - Fee Related
-
1999
- 1999-11-13 KR KR10-1999-0050406A patent/KR100409137B1/en active IP Right Grant
Also Published As
| Publication number | Publication date |
|---|---|
| KR20000035463A (en) | 2000-06-26 |
| KR100409137B1 (en) | 2003-12-11 |
| JP2000144341A (en) | 2000-05-26 |
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