JPH0561346B2 - - Google Patents
Info
- Publication number
- JPH0561346B2 JPH0561346B2 JP5199286A JP5199286A JPH0561346B2 JP H0561346 B2 JPH0561346 B2 JP H0561346B2 JP 5199286 A JP5199286 A JP 5199286A JP 5199286 A JP5199286 A JP 5199286A JP H0561346 B2 JPH0561346 B2 JP H0561346B2
- Authority
- JP
- Japan
- Prior art keywords
- iron
- chromium
- molybdenum
- base
- alloy
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Fee Related
Links
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 81
- 229910045601 alloy Inorganic materials 0.000 claims description 63
- 239000000956 alloy Substances 0.000 claims description 63
- 239000011651 chromium Substances 0.000 claims description 43
- 229910052742 iron Inorganic materials 0.000 claims description 37
- 229910052804 chromium Inorganic materials 0.000 claims description 23
- 229910052750 molybdenum Inorganic materials 0.000 claims description 20
- 239000002245 particle Substances 0.000 claims description 20
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 18
- 239000011572 manganese Substances 0.000 claims description 17
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 15
- 239000011733 molybdenum Substances 0.000 claims description 15
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 14
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 12
- 229910052799 carbon Inorganic materials 0.000 claims description 10
- 229910052748 manganese Inorganic materials 0.000 claims description 9
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 8
- 239000000314 lubricant Substances 0.000 claims description 7
- 229910052721 tungsten Inorganic materials 0.000 claims description 7
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims description 7
- 239000007787 solid Substances 0.000 claims description 6
- WUKWITHWXAAZEY-UHFFFAOYSA-L calcium difluoride Chemical compound [F-].[F-].[Ca+2] WUKWITHWXAAZEY-UHFFFAOYSA-L 0.000 claims description 5
- 239000011159 matrix material Substances 0.000 claims description 5
- CADICXFYUNYKGD-UHFFFAOYSA-N sulfanylidenemanganese Chemical compound [Mn]=S CADICXFYUNYKGD-UHFFFAOYSA-N 0.000 claims description 5
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 claims description 5
- 239000010937 tungsten Substances 0.000 claims description 5
- 239000010941 cobalt Substances 0.000 claims description 4
- 229910017052 cobalt Inorganic materials 0.000 claims description 4
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims description 4
- 239000012535 impurity Substances 0.000 claims description 4
- CWQXQMHSOZUFJS-UHFFFAOYSA-N molybdenum disulfide Chemical compound S=[Mo]=S CWQXQMHSOZUFJS-UHFFFAOYSA-N 0.000 claims description 4
- 229910052982 molybdenum disulfide Inorganic materials 0.000 claims description 4
- 229910052759 nickel Inorganic materials 0.000 claims description 4
- 230000000694 effects Effects 0.000 description 16
- 230000013011 mating Effects 0.000 description 13
- 239000000463 material Substances 0.000 description 10
- 230000008595 infiltration Effects 0.000 description 5
- 238000001764 infiltration Methods 0.000 description 5
- 239000000843 powder Substances 0.000 description 5
- QGZKDVFQNNGYKY-UHFFFAOYSA-N Ammonia Chemical compound N QGZKDVFQNNGYKY-UHFFFAOYSA-N 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 229910052720 vanadium Inorganic materials 0.000 description 3
- 229910021529 ammonia Inorganic materials 0.000 description 2
- 238000002485 combustion reaction Methods 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000000354 decomposition reaction Methods 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000009792 diffusion process Methods 0.000 description 2
- 229910002804 graphite Inorganic materials 0.000 description 2
- 239000010439 graphite Substances 0.000 description 2
- 230000001050 lubricating effect Effects 0.000 description 2
- 238000005245 sintering Methods 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 229910004261 CaF 2 Inorganic materials 0.000 description 1
- 229910001018 Cast iron Inorganic materials 0.000 description 1
- 229910001021 Ferroalloy Inorganic materials 0.000 description 1
- 229910001309 Ferromolybdenum Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 229910001634 calcium fluoride Inorganic materials 0.000 description 1
- 125000002915 carbonyl group Chemical group [*:2]C([*:1])=O 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- GPPXJZIENCGNKB-UHFFFAOYSA-N vanadium Chemical compound [V]#[V] GPPXJZIENCGNKB-UHFFFAOYSA-N 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)
Description
〔産業上の利用分野〕
本発明は内燃機関のバルブシート用焼結合金に
係わり、より詳しくは合金自身の耐摩耗性を高め
るとともに、相手バルブに対する攻撃性を弱めた
鉄系焼結合金に関する。
〔従来の技術〕
最近、自動車用内燃機関は高出力、高回転化、
低燃費化が計られ、また排気ガス対策が施される
傾向にある。このため、バルブやバルブシート部
品は従来以上に厳しい条件にさらされるようにな
つてきている。
このバルブシートには高温での耐摩耗性を高め
るため、Cr，Ni，Co，Mo等の合金元素を添加
した鉄系焼結合金が多用されつつある。
〔発明が解決しようとする問題点〕
ところで、バルブシートは、自身の耐摩耗性を
向上させるとともに相手バルブへの攻撃性の低減
が求められており、バルブシートの材質の選択
は、相手バルブとの相関において決定されるべき
もので、この選択を誤るとバルブ自身の耐摩耗性
を弱めるばかりか、相手部材に対する攻撃性を増
して、バルブ機構全体に思わしくない影響を与え
ることになる。そのため従来のような、例えばた
だ単にフエロモリブデン等の金属間化合物又は複
合炭化物を添加して極度に耐摩耗性を高めたバル
ブシートをそのまま使用すると、エンジンバルブ
の摩耗を増大させる結果となる。
本発明は通常の、耐摩耗性が特に高められてい
ない汎用エンジンバルブ（例えばJISNFC751製）
を相手にした場合にも相手材を摩耗することな
く、又は自身の摩耗を著しく増大させることのな
いようにしようとするものである。
〔問題点を解決するための手段〕
本発明のバルブシート用鉄系焼結合金は、重量
比で、クロム（Cr），モリブデン（Mo），バナジ
ウム（Ｖ）、及びマンガン（Mn）からなる群か
ら選ばれる元素１種または２種以上１〜20％、炭
素（Ｃ）0.5〜２％及び不可避不純物を含む鉄基
合金を基地とし、クロム（Cr）10〜70％，タン
グステン（Ｗ）５〜20％，モリブデン（Mo）５
〜20％，鉄（Fe）20％以下、炭素（Ｃ）0.5〜３
％及び残部コバルト（Co）からなる合金粒子５
〜25％並びにフツ化カルシウム（CaF2），二硫化
モリブデン（MoS2）及び硫化マンガン（MnS）
からなる群から選ばれる固体潤滑剤１種または２
種以上0.2〜３％を基地中に均一に分散させたこ
とを特徴とする。
また、本発明は、基地が上記の成分に加えてニ
ツケル（Ni）１〜10％を含む鉄基合金であるバ
ルブシート用焼結合金にも関する。
さらに、本発明は前記焼結合金に鉛（Pb）１
〜20％を溶浸したことを特徴とする。
なお、本発明において％は特記しない限り重量
％を示す。
本発明で用いる各成分元素の限定理由について
説明する。
まず、硬質粒子として加える合金粒子の各成分
元素について説明する。
合金粒子中のクロム（Cr）はＣ（炭素）と化合
して炭化物を形成するとともに一部がCoと合金
を形成し合金粒子の硬さを向上させる効果を有し
ているが、Crが10％未満では上記の効果が不十
分であり、70％を超えるとCrの拡散が周囲の基
地へ進み過ぎ、合金粒子の内部及び周縁に空隙を
生じ、合金粒子がもろくなる。そのためCrは10
〜70％と限定した。
Ｗ（タングステン）は、Ｃと化合してMC型の
硬質炭化物とCoとの複炭化物を形成し、合金粒
子の硬さを向上させるが、Ｗが５％未満ではその
効果が発揮されず、20％を超えると合金粒子が硬
くなり過ぎ、相手材であるバルブへの攻撃性が増
大するため、Ｗは５〜20％とした。
Mo（モリブデン）はＣと化合して硬質炭化物
を形成し、合金粒子の硬さを増すが、Moが５％
未満ではその効果が現れず、20％を超えると合金
粒子が硬くなり過ぎて相手部材を攻撃するので５
〜20％とした。
ＣはCr，Mo及びＷと化合して炭化物を形成
し、合金粒子の硬さを向上させるが、Ｃは0.5％
未満ではその効果が発揮されず、３％を超えると
炭化物量が多すぎてもろくなる。そのため、Ｃは
0.5〜３％とした。
Fe（鉄）は特に添加しなくてもよいが、バルブ
シートに必要とする強度等に問題がなければ、高
価なCoの代わりに20％以下の任意の範囲で用い
ることができる。また、Cr，Ｗ，Moを単体とし
てではなくフエロアロイとして合金の原料に用い
る場合に添加されることになる。
合金粒子は耐摩耗性の向上に効果があることか
ら用いられる。その粒径は30〜150μmが好まし
く、合金中のCoの一部が基地中に拡散して粒子
の周囲に拡散層を形成することによつて、粒子と
基地との結合力が増し、該粒子の脱落が防止され
る。該合金粒子は５％未満では得られる焼結合金
の耐摩耗効果が発揮されず、25％を超えると成形
性、圧縮性及び被削性が低下するとともに相手材
であるバルブへの攻撃性が増大するため、合金粒
子は５〜25％と限定した。
次に固体潤滑剤について説明する。本発明にお
いては、固体潤滑剤としてCaF2，MoS2及び
MnSからなる群より選ばれる化合物の一種もし
くは二種以上を使用しており、これらの物質は基
地中に分散され、その潤滑作用により摺動面にお
けるバルブ及びバルブシートの摩耗を低減する
が、0.2％未満では効果がなく、３％を超えても
効果の向上が認められずに単にコスト高を起こす
結果となるため、0.2〜３％とした。
次に基地について説明する。
Cr，Mo，Ｖ（バナジウム），Mn（マンガン）の
１種又は２種以上を含む鉄基合金の１種又は２種
以上を使用することにより、鉄基地の耐熱性及び
耐食性を向上させることができる。特に、Cr1〜
５％，Mo0.1〜１％及びV0.1〜１％を含む鉄基合
金、Cr0.5〜２％、Mo0.1〜１％及びMn0.1〜１
％を含む鉄基合金又はCr6〜18を含む鉄基合金を
使用することが好ましい。上記鉄基合金中に含ま
れるCr，Mo，Ｖ，Mnの１種又は２種以上は１
％未満では鉄基地の耐熱性・耐食性の向上に対す
る効果がなく、20％超えてもそれ以上の効果が得
られないため、１〜20％とした。
Ｃは上記鉄基合金中に拡散して焼結を促進さ
せ、基地を強化させる効果があるとともに、未反
応の遊離黒鉛が、ある程度基地中に内在すること
により、潤滑効果が発揮されるが、Ｃが0.5％未
満ではその効果がなく、2.0％を超えるとセメン
タイトが析出し、基地がもろくなつたり、遊離黒
鉛が多すぎて基地の強度が低下するため、Ｃは
0.5〜２％とした。
Ni（ニツケル）はFe基地に固溶して基地の強度
を向上させるのに役立つため、更に強度を必要と
する場合に添加されるが、Niが１％未満ではそ
の効果が発揮されず、10％を超えると基地が軟化
し、耐摩耗性が低下するため、Niは１〜10％と
した。
Pb（鉛）の焼結合金への溶浸は、よりきびしい
条件下で使用されるバルブシートの場合に行われ
る。溶浸されたPbは、バルブとバルブシートの
接触部に介在してPb酸化物層を形成することに
より潤滑剤として作用してバルブ及びバルブシー
ト相互の耐摩耗性を向上させるが、Pbの溶浸が
１％未満ではPb溶浸の効果が発揮されず、20％
を超えて溶浸すると焼結合金のスケルトンが弱化
して摩耗が増大することから１〜20％とした。
〔実施例〕
以下、実施例にもとづいて本発明をさらに詳細
に説明する。
実施例 １
Cr45％，W17％，Mo10％，Fe15％，Ｃ：1.5
％及び残部Coからなる合金アトマイズ粉末（−
100メツシユ）10％、黒鉛粉末（−350メツシユ）
1.1％、カルボニルNi粉末（10μm以下）２％，
CaF20.5％、並びに残部としてCr12％及び残部Fe
からなる合金アトマイズ鉄粉（−100メツシユ）
からなる焼結用粉末組成物にステアリン酸亜鉛粉
末0.8％を混合した後、この混合粉末を金型内に
充てんし、成形圧7t／cm2で成形してバルブシート
粗形状の粉末成形体を得た。
この粉末成形体をアンモニア分解ガス雰囲気中
で1150℃の温度にて60分間焼結して焼結体を得
た。焼結体密度は6.9ｇ／cm3である。
得られた焼結体を排気バルブシートの形状に加
工して排気量2000c.c.４気筒のデイーゼルエンジン
に装着し、全負荷で200時間台上耐久試験を実施
し、バルブシート当り面幅増加量及びバルブ摩耗
量を測定した。なお、相手バルブにはJIS
NFC751を用いた。
実施例 ２〜８
各材料を表１及び表２に示す各組成割合にそれ
ぞれ配合して実施例１と同様に行つて、各焼結体
を得た。なお、実施例３，４，６及び８は得られ
た焼結体をPb塊と接触させて再度アンモニア分
解ガス雰囲気中で1050℃の温度にて30分間加熱し
て焼結体中にPbを溶浸したものである。
得られた各焼結体をバルブシート形状に加工
し、バルブシート当り面幅増加量及びバルブ摩耗
量を実施例１と同様に試験したのち測定した。
比較例 １及び２
比較例１としてJIS FC30鋳鉄、比較例２とし
てJIS耐熱鋼材SUH4Bをそれぞれ用いてバルブ
シート形状に加工し、これらを実施例１と同様に
試験してバルブ摩耗量を測定した。
以上の測定結果をまとめて表１に示す。
[Industrial Application Field] The present invention relates to a sintered alloy for a valve seat of an internal combustion engine, and more particularly to an iron-based sintered alloy that has improved wear resistance of the alloy itself and is less aggressive to a mating valve. [Conventional technology] Recently, automobile internal combustion engines have become more powerful, have higher rotation speeds,
There is a trend toward lower fuel consumption and measures against exhaust gas. For this reason, valves and valve seat components are being exposed to more severe conditions than ever before. In order to improve wear resistance at high temperatures, iron-based sintered alloys containing alloying elements such as Cr, Ni, Co, and Mo are increasingly being used for valve seats. [Problems to be solved by the invention] By the way, the valve seat is required to improve its own wear resistance and reduce its aggressiveness to the mating valve, and the selection of the material of the valve seat is dependent on the mating valve. If this selection is incorrect, it will not only weaken the wear resistance of the valve itself, but also increase its aggressiveness against the mating member, which will have an undesirable effect on the entire valve mechanism. Therefore, if a conventional valve seat, for example, which has extremely high wear resistance by simply adding an intermetallic compound such as ferromolybdenum or a composite carbide, is used as it is, the wear of the engine valve will increase. The present invention applies to ordinary, general-purpose engine valves whose wear resistance is not particularly enhanced (for example, manufactured by JISNFC751).
The aim is to avoid abrasion of the mating material or a significant increase in wear of the mating material even when the mating material is used as a mating material. [Means for Solving the Problems] The iron-based sintered alloy for valve seats of the present invention has a weight ratio of chromium (Cr), molybdenum (Mo), vanadium (V), and manganese (Mn). Based on an iron-based alloy containing 1 to 20% of one or more elements selected from the following, 0.5 to 2% of carbon (C), and unavoidable impurities, 10 to 70% of chromium (Cr), 5 to 5% of tungsten (W). 20%, Molybdenum (Mo) 5
~20%, Iron (Fe) 20% or less, Carbon (C) 0.5-3
Alloy particles 5 consisting of % and balance cobalt (Co)
~25% and calcium fluoride (CaF 2 ), molybdenum disulfide (MoS 2 ) and manganese sulfide (MnS)
1 or 2 solid lubricants selected from the group consisting of
It is characterized by having 0.2 to 3% of seeds uniformly dispersed throughout the base. The present invention also relates to a sintered alloy for a valve seat in which the base is an iron-based alloy containing 1 to 10% of nickel (Ni) in addition to the above-mentioned components. Furthermore, the present invention includes lead (Pb) 1 in the sintered alloy.
Characterized by ~20% infiltration. In the present invention, % indicates weight % unless otherwise specified. The reason for limiting each component element used in the present invention will be explained. First, each component element of the alloy particles added as hard particles will be explained. Chromium (Cr) in the alloy particles combines with C (carbon) to form carbides, and a portion also forms an alloy with Co, which has the effect of improving the hardness of the alloy particles. If it is less than 70%, the above effect is insufficient, and if it exceeds 70%, the diffusion of Cr will proceed too much to the surrounding base, creating voids inside and at the periphery of the alloy particles, making the alloy particles brittle. Therefore Cr is 10
Limited to ~70%. W (tungsten) combines with C to form a double carbide of MC-type hard carbide and Co, improving the hardness of the alloy particles, but this effect is not exhibited when W is less than 5%. If the W content exceeds 5%, the alloy particles become too hard and attack against the valve, which is the mating material, increases, so W is set at 5 to 20%. Mo (molybdenum) combines with C to form hard carbides and increases the hardness of alloy particles, but Mo
If it is less than 20%, the effect will not appear, and if it exceeds 20%, the alloy particles will become too hard and attack the mating material.
~20%. C combines with Cr, Mo and W to form carbides and improves the hardness of alloy particles, but C is 0.5%
If it is less than 3%, the effect will not be exhibited, and if it exceeds 3%, the amount of carbide will be too large and it will become brittle. Therefore, C is
It was set at 0.5 to 3%. Fe (iron) does not need to be particularly added, but if there is no problem with the strength required for the valve seat, it can be used in any range of 20% or less in place of the expensive Co. Further, when Cr, W, and Mo are used as raw materials for alloys as ferroalloys rather than as single substances, they are added. Alloy particles are used because they are effective in improving wear resistance. The particle size is preferably 30 to 150 μm, and a part of the Co in the alloy diffuses into the matrix to form a diffusion layer around the particles, increasing the bonding force between the particles and the matrix. is prevented from falling off. If the alloy particles are less than 5%, the resulting sintered alloy will not exhibit its wear-resistance effect, and if it exceeds 25%, the formability, compressibility, and machinability will decrease, and the mating material, the valve, will be attacked. Because of this, the alloy particles were limited to 5-25%. Next, solid lubricants will be explained. In the present invention, CaF 2 , MoS 2 and
One or more compounds selected from the group consisting of MnS are used, and these substances are dispersed in the base, and their lubricating action reduces wear of valves and valve seats on sliding surfaces, but 0.2 If it is less than 3%, there is no effect, and if it exceeds 3%, no improvement in the effect will be observed and the cost will simply increase, so it was set at 0.2 to 3%. Next, I will explain about the base. By using one or more iron-based alloys containing one or more of Cr, Mo, V (vanadium), and Mn (manganese), the heat resistance and corrosion resistance of the iron base can be improved. can. In particular, Cr1~
5%, Mo0.1~1% and V0.1~1%, Cr0.5~2%, Mo0.1~1% and Mn0.1~1
It is preferable to use iron-based alloys containing Cr6-18%. One or more of Cr, Mo, V, and Mn contained in the above iron-based alloy is 1
If it is less than 20%, there is no effect on improving the heat resistance and corrosion resistance of the iron base, and if it exceeds 20%, no further effect can be obtained, so it was set at 1 to 20%. C diffuses into the iron-based alloy, promotes sintering, and has the effect of strengthening the matrix, and a certain amount of unreacted free graphite remains in the matrix, thereby exerting a lubricating effect. If C is less than 0.5%, it has no effect, and if it exceeds 2.0%, cementite will precipitate, making the base brittle, or there will be too much free graphite, reducing the strength of the base.
It was set at 0.5 to 2%. Ni (nickel) dissolves in the Fe base and helps improve the strength of the base, so it is added when further strength is required, but if Ni is less than 1%, its effect will not be exhibited, and 10 If the Ni content exceeds 1%, the base becomes soft and the wear resistance decreases, so the Ni content was set to 1 to 10%. Infiltration of sintered alloys with Pb (lead) is carried out in the case of valve seats used under more severe conditions. The infiltrated Pb acts as a lubricant by forming a Pb oxide layer at the contact area between the valve and the valve seat, improving mutual wear resistance between the valve and the valve seat. If the Pb infiltration is less than 1%, the effect of Pb infiltration will not be exhibited;
If infiltration exceeds 1%, the skeleton of the sintered alloy will weaken and wear will increase, so it was set at 1% to 20%. [Example] Hereinafter, the present invention will be explained in more detail based on Examples. Example 1 Cr45%, W17%, Mo10%, Fe15%, C: 1.5
Alloy atomized powder (−
100 mesh) 10%, graphite powder (-350 mesh)
1.1%, carbonyl Ni powder (10 μm or less) 2%,
CaF2 0.5%, balance Cr12% and balance Fe
Alloy atomized iron powder consisting of (-100 mesh)
After mixing 0.8% zinc stearate powder into a sintering powder composition consisting of Obtained. This powder compact was sintered at a temperature of 1150°C for 60 minutes in an ammonia decomposition gas atmosphere to obtain a sintered body. The density of the sintered body is 6.9 g/cm 3 . The obtained sintered body was processed into the shape of an exhaust valve seat, installed in a 2000 c.c. 4-cylinder diesel engine, and subjected to a 200-hour bench durability test under full load, which increased the surface width per valve seat. The amount of wear and valve wear were measured. In addition, the mating valve is JIS
NFC751 was used. Examples 2 to 8 Each material was blended in the respective composition ratios shown in Tables 1 and 2, and the same procedure as in Example 1 was carried out to obtain each sintered body. In Examples 3, 4, 6 and 8, the obtained sintered body was brought into contact with a Pb lump and heated again at a temperature of 1050°C for 30 minutes in an ammonia decomposition gas atmosphere to release Pb into the sintered body. It is infiltrated. Each of the obtained sintered bodies was processed into a valve seat shape, and the amount of increase in surface width per valve seat and the amount of valve wear were tested and measured in the same manner as in Example 1. Comparative Examples 1 and 2 JIS FC30 cast iron as Comparative Example 1 and JIS heat-resistant steel SUH4B as Comparative Example 2 were processed into valve seat shapes, and these were tested in the same manner as in Example 1 to measure the amount of valve wear. The above measurement results are summarized in Table 1.
【表】
＊ 組成は表２に示す。
[Table] *The composition is shown in Table 2.
本発明のバルブシート用鉄系焼結合金は上記に
示したように合金粒子と固体潤滑剤を鉄基合金基
地に均一に分散させたものであるため、耐摩耗性
に優れ、かつ相手材であるバルブに対する攻撃性
が低く、バルブシート用焼結合金として最適なも
のである。
As shown above, the iron-based sintered alloy for valve seats of the present invention has alloy particles and solid lubricant uniformly dispersed in the iron-based alloy base, so it has excellent wear resistance and is superior to the mating material. It has low aggressiveness against certain valves and is optimal as a sintered alloy for valve seats.
Claims (1)
（Mo）、バナジウム（Ｖ）、及びマンガン（Mn）
からなる群から選ばれる元素１種または２種以上
１〜20％、炭素（Ｃ）0.5〜２％及び不可避不純
物を含む鉄基合金を基地とし、クロム（Cr）10
〜70％、タングステン（Ｗ）５〜20％、モリブデ
ン（Mo）５〜20％、鉄（Fe）20％以下、炭素
（Ｃ）0.5〜３％及び残部コバルト（Co）からなる
合金粒子５〜25％並びにフツ化カルシウム
（CaF2）、二硫化モリブデン（MoS2）及び硫化マ
ンガン（MnS）からなる群から選ばれる固体潤
滑剤１種または２種以上0.2〜３％を基地中に均
一に分散させたことを特徴とするバルブシート用
鉄系焼結合金。 ２ 基地が、重量比で、クロム（Cr）１〜５％、
モリブデン（Mo）0.1〜１％及びバナジウム
（Ｖ）0.1〜１％を含む鉄基合金であることを特徴
とする特許請求の範囲第１項記載のバルブシート
用鉄系焼結合金。 ３ 基地が、重量比で、クロム（Cr）0.5〜２％、
モリブデン（Mo）0.1〜１％及びマンガン（Mn）
0.1〜１％を含む鉄基合金であることを特徴とす
る特許請求の範囲第１項記載のバルブシート用鉄
系焼結合金。 ４ 基地が、重量比で６〜18％のクロム（Cr）
を含む鉄基合金であることを特徴とする特許請求
の範囲第１項記載のバルブシート用鉄系焼結合
金。 ５ 重量比で、クロム（Cr）、モリブデン
（Mo）、バナジウム（Ｖ）、及びマンガン（Mn）
からなる群から選ばれる元素１種または２種以上
１〜20％、炭素（Ｃ）0.5〜２％、ニツケル（Ni）
１〜10％及び不可避不純物を含む鉄基合金を基地
とし、クロム（Cr）10〜70％、タングステン
（Ｗ）５〜20％、モリブデン（Mo）５〜20％、
鉄（Fe）20％以下、炭素（Ｃ）0.5〜３％及び残
部コバルト（Co）からなる合金粒子５〜25％並
びにフツ化カルシウム（CaF2）、二硫化モリブデ
ン（MoS2）及び硫化マンガン（MnS）からなる
群から選ばれる固体潤滑剤１種または２種以上
0.2〜３％を基地中に均一に分散させたことを特
徴とするバルブシート用鉄系焼結合金。 ６ 基地が、重量比で、クロム（Cr）１〜５％、
モリブデン（Mo）0.1〜１％及びバナジウム
（Ｖ）0.1〜１％を含む鉄基合金であることを特徴
とする特許請求の範囲第５項記載のバルブシート
用鉄系焼結合金。 ７ 基地が、重量比で、クロム（Cr）0.5〜２％、
モリブデン（Mo）0.1〜１％及びマンガン（Mn）
0.1〜１％を含む鉄基合金であることを特徴とす
る特許請求の範囲第５項記載のバルブシート用鉄
系焼結合金。 ８ 基地が、重量比で６〜18％のクロム（Cr）
を含む鉄基合金であることを特徴とする特許請求
の範囲第５項記載のバルブシート用鉄系焼結合
金。 ９ 重量比で、クロム（Cr）、モリブデン
（Mo）、バナジウム（Ｖ）、及びマンガン（Mn）
からなる群から選ばれる元素１種または２種以上
１〜20％、炭素（Ｃ）0.5〜２％及び不可避不純
物を含む鉄基合金を基地とし、クロム（Cr）10
〜70％、タングステン（Ｗ）５〜20％、モリブデ
ン（Mo）５〜20％、鉄（Fe）20％以下、炭素
（Ｃ）0.5〜３％及び残部コバルト（Co）からなる
合金粒子５〜25％並びにフツ化カルシウム
（CaF2）、二硫化モリブデン（MoS2）及び硫化マ
ンガン（MnS）からなる群から選ばれる固体潤
滑剤１種または２種以上0.2〜３％を基地中に均
一に分散してなる焼結合金に鉛（Pb）１〜20％
を溶浸したことを特徴とするバルブシート用鉄系
焼結合金。 １０ 基地が、重量比で、クロム（Cr）１〜５
％、モリブデン（Mo）0.1〜１％及びバナジウム
（Ｖ）0.1〜１％を含む鉄基合金であることを特徴
とする特許請求の範囲第９項記載のバルブシート
用鉄系焼結合金。 １１ 基地が、重量比で、クロム（Cr）0.5〜２
％、モリブデン（Mo）0.1〜１％及びマンガン
（Mn）0.1〜１％を含む鉄基合金であることを特
徴とする特許請求の範囲第９項記載のバルブシー
ト用鉄系焼結合金。 １２ 基地が、重量比で６〜18％のクロム（Cr）
を含む鉄基合金であることを特徴とする特許請求
の範囲第９項記載のバルブシート用鉄系焼結合
金。[Claims] 1 Chromium (Cr), molybdenum (Mo), vanadium (V), and manganese (Mn) in weight ratio
Based on an iron-based alloy containing 1 to 20% of one or more elements selected from the group consisting of, 0.5 to 2% of carbon (C) and unavoidable impurities, chromium (Cr) 10
~70%, tungsten (W) 5~20%, molybdenum (Mo) 5~20%, iron (Fe) 20% or less, carbon (C) 0.5~3%, and balance cobalt (Co) 5~ 25% and 0.2 to 3% of one or more solid lubricants selected from the group consisting of calcium fluoride (CaF 2 ), molybdenum disulfide (MoS 2 ), and manganese sulfide (MnS) are uniformly dispersed in the base. An iron-based sintered alloy for valve seats, which is characterized by: 2 The base is chromium (Cr) 1 to 5% by weight,
The iron-based sintered alloy for a valve seat according to claim 1, which is an iron-based alloy containing 0.1 to 1% of molybdenum (Mo) and 0.1 to 1% of vanadium (V). 3 The base is chromium (Cr) 0.5 to 2% by weight,
Molybdenum (Mo) 0.1-1% and manganese (Mn)
The iron-based sintered alloy for a valve seat according to claim 1, characterized in that it is an iron-based alloy containing 0.1 to 1%. 4 The base is 6 to 18% chromium (Cr) by weight
The iron-based sintered alloy for a valve seat according to claim 1, wherein the iron-based sintered alloy is an iron-based alloy containing. 5 Chromium (Cr), molybdenum (Mo), vanadium (V), and manganese (Mn) in weight ratio
1-20% of one or more elements selected from the group consisting of, carbon (C) 0.5-2%, nickel (Ni)
Based on iron-based alloy containing 1-10% and unavoidable impurities, chromium (Cr) 10-70%, tungsten (W) 5-20%, molybdenum (Mo) 5-20%,
Alloy particles consisting of 20% or less of iron (Fe), 0.5 to 3% of carbon (C), and the balance of cobalt (Co), calcium fluoride (CaF 2 ), molybdenum disulfide (MoS 2 ), and manganese sulfide ( One or more solid lubricants selected from the group consisting of
An iron-based sintered alloy for valve seats, characterized in that 0.2 to 3% is uniformly dispersed in the matrix. 6 The base is chromium (Cr) 1 to 5% by weight,
The iron-based sintered alloy for a valve seat according to claim 5, which is an iron-based alloy containing 0.1 to 1% of molybdenum (Mo) and 0.1 to 1% of vanadium (V). 7 The base is chromium (Cr) 0.5 to 2% by weight,
Molybdenum (Mo) 0.1-1% and manganese (Mn)
The iron-based sintered alloy for a valve seat according to claim 5, characterized in that it is an iron-based alloy containing 0.1 to 1%. 8 Base is 6-18% chromium (Cr) by weight
The iron-based sintered alloy for a valve seat according to claim 5, wherein the iron-based sintered alloy is an iron-based alloy containing. 9 Chromium (Cr), molybdenum (Mo), vanadium (V), and manganese (Mn) in weight ratio
Based on an iron-based alloy containing 1 to 20% of one or more elements selected from the group consisting of, 0.5 to 2% of carbon (C) and unavoidable impurities, chromium (Cr) 10
~70%, tungsten (W) 5~20%, molybdenum (Mo) 5~20%, iron (Fe) 20% or less, carbon (C) 0.5~3%, and balance cobalt (Co) 5~ 25% and 0.2 to 3% of one or more solid lubricants selected from the group consisting of calcium fluoride (CaF 2 ), molybdenum disulfide (MoS 2 ), and manganese sulfide (MnS) are uniformly dispersed in the base. 1 to 20% lead (Pb) in the sintered alloy made by
An iron-based sintered alloy for valve seats, characterized by being infiltrated with. 10 Base is chromium (Cr) 1 to 5 in weight ratio
%, molybdenum (Mo) 0.1 to 1%, and vanadium (V) 0.1 to 1%. 11 The base has a weight ratio of chromium (Cr) of 0.5 to 2
%, molybdenum (Mo) 0.1 to 1%, and manganese (Mn) 0.1 to 1%. 12 The base is 6 to 18% chromium (Cr) by weight
The iron-based sintered alloy for a valve seat according to claim 9, wherein the iron-based sintered alloy is an iron-based alloy containing.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5199286A JPS62207847A (en) | 1986-03-10 | 1986-03-10 | Ferrous sintered alloy for valve seat |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5199286A JPS62207847A (en) | 1986-03-10 | 1986-03-10 | Ferrous sintered alloy for valve seat |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS62207847A JPS62207847A (en) | 1987-09-12 |
| JPH0561346B2 true JPH0561346B2 (en) | 1993-09-06 |
Family
ID=12902348
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP5199286A Granted JPS62207847A (en) | 1986-03-10 | 1986-03-10 | Ferrous sintered alloy for valve seat |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS62207847A (en) |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2787982B2 (en) * | 1987-03-31 | 1998-08-20 | 住友電気工業株式会社 | Wear resistant iron-based sintered alloy |
| JPH0826764B2 (en) * | 1987-12-29 | 1996-03-21 | 株式会社リケン | Method for manufacturing valve seat made of iron-based sintered alloy |
| JP6671772B2 (en) * | 2015-12-22 | 2020-03-25 | 山陽特殊製鋼株式会社 | High hardness and toughness powder |
-
1986
- 1986-03-10 JP JP5199286A patent/JPS62207847A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS62207847A (en) | 1987-09-12 |
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