JP2003213308A - Sintered cast iron sliding member and its producing method - Google Patents
Sintered cast iron sliding member and its producing methodInfo
- Publication number
- JP2003213308A JP2003213308A JP2002007371A JP2002007371A JP2003213308A JP 2003213308 A JP2003213308 A JP 2003213308A JP 2002007371 A JP2002007371 A JP 2002007371A JP 2002007371 A JP2002007371 A JP 2002007371A JP 2003213308 A JP2003213308 A JP 2003213308A
- Authority
- JP
- Japan
- Prior art keywords
- cast iron
- chips
- sliding member
- mesh screen
- range
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 229910001018 Cast iron Inorganic materials 0.000 title claims abstract description 45
- 238000000034 method Methods 0.000 title claims description 25
- 229910001060 Gray iron Inorganic materials 0.000 claims abstract description 46
- 238000005266 casting Methods 0.000 claims abstract description 40
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 35
- 239000000956 alloy Substances 0.000 claims abstract description 35
- 238000005520 cutting process Methods 0.000 claims abstract description 30
- 238000005245 sintering Methods 0.000 claims abstract description 10
- 239000000843 powder Substances 0.000 claims abstract description 8
- 239000000463 material Substances 0.000 claims description 53
- 239000011248 coating agent Substances 0.000 claims description 28
- 238000000576 coating method Methods 0.000 claims description 28
- 238000011282 treatment Methods 0.000 claims description 26
- 238000010438 heat treatment Methods 0.000 claims description 20
- 239000003921 oil Substances 0.000 claims description 18
- 239000010687 lubricating oil Substances 0.000 claims description 17
- 238000004519 manufacturing process Methods 0.000 claims description 15
- 239000011812 mixed powder Substances 0.000 claims description 13
- 238000005470 impregnation Methods 0.000 claims description 11
- 238000000465 moulding Methods 0.000 claims description 9
- 230000009466 transformation Effects 0.000 claims description 8
- 238000001816 cooling Methods 0.000 claims description 7
- 238000000748 compression moulding Methods 0.000 claims description 6
- 230000007935 neutral effect Effects 0.000 claims description 6
- 238000011068 loading method Methods 0.000 claims description 2
- 239000002245 particle Substances 0.000 description 29
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 28
- 239000010439 graphite Substances 0.000 description 21
- 229910002804 graphite Inorganic materials 0.000 description 21
- 230000000052 comparative effect Effects 0.000 description 18
- SZVJSHCCFOBDDC-UHFFFAOYSA-N ferrosoferric oxide Chemical compound O=[Fe]O[Fe]O[Fe]=O SZVJSHCCFOBDDC-UHFFFAOYSA-N 0.000 description 18
- 229940056319 ferrosoferric oxide Drugs 0.000 description 9
- 230000001186 cumulative effect Effects 0.000 description 8
- 230000013011 mating Effects 0.000 description 8
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 6
- 230000001050 lubricating effect Effects 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- 229910000859 α-Fe Inorganic materials 0.000 description 5
- 229910052799 carbon Inorganic materials 0.000 description 4
- 239000004519 grease Substances 0.000 description 4
- 238000005461 lubrication Methods 0.000 description 4
- 239000011572 manganese Substances 0.000 description 4
- 229910000975 Carbon steel Inorganic materials 0.000 description 3
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 3
- 239000010962 carbon steel Substances 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 229910052698 phosphorus Inorganic materials 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- 238000010791 quenching Methods 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- 229910052717 sulfur Inorganic materials 0.000 description 3
- 238000010998 test method Methods 0.000 description 3
- QGZKDVFQNNGYKY-UHFFFAOYSA-N Ammonia Chemical compound N QGZKDVFQNNGYKY-UHFFFAOYSA-N 0.000 description 2
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 2
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 2
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 2
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 2
- 230000002159 abnormal effect Effects 0.000 description 2
- 230000006835 compression Effects 0.000 description 2
- 238000007906 compression Methods 0.000 description 2
- 230000003247 decreasing effect Effects 0.000 description 2
- 238000000227 grinding Methods 0.000 description 2
- UQSXHKLRYXJYBZ-UHFFFAOYSA-N iron oxide Inorganic materials [Fe]=O UQSXHKLRYXJYBZ-UHFFFAOYSA-N 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 238000002156 mixing Methods 0.000 description 2
- NDLPOXTZKUMGOV-UHFFFAOYSA-N oxo(oxoferriooxy)iron hydrate Chemical compound O.O=[Fe]O[Fe]=O NDLPOXTZKUMGOV-UHFFFAOYSA-N 0.000 description 2
- 239000011574 phosphorus Substances 0.000 description 2
- 238000007789 sealing Methods 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 239000010703 silicon Substances 0.000 description 2
- 239000000758 substrate Substances 0.000 description 2
- 239000011593 sulfur Substances 0.000 description 2
- 101100219325 Phaseolus vulgaris BA13 gene Proteins 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 229910021529 ammonia Inorganic materials 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005261 decarburization Methods 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- 239000012530 fluid Substances 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 239000010721 machine oil Substances 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 239000002480 mineral oil Substances 0.000 description 1
- 235000010446 mineral oil Nutrition 0.000 description 1
- 239000010705 motor oil Substances 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
Classifications
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02W—CLIMATE CHANGE MITIGATION TECHNOLOGIES RELATED TO WASTEWATER TREATMENT OR WASTE MANAGEMENT
- Y02W30/00—Technologies for solid waste management
- Y02W30/50—Reuse, recycling or recovery technologies
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、成長ねずみ鋳鉄鋳
物を切削して得られた切粉を使用した鋳鉄系焼結摺動部
材及びその製造方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a cast iron-based sintered sliding member using chips obtained by cutting a grown gray cast iron casting and a method for manufacturing the same.
【０００２】[0002]
【従来の技術】従来から、炭素が片状黒鉛の形で存在し
ているねずみ鋳鉄が知られている。このねずみ鋳鉄から
作製された鋳物（ねずみ鋳鉄鋳物）は、大きな振動吸収
能と高い熱伝導性を有することから内燃機関用材料とし
て広く用いられている。また、ねずみ鋳鉄は優れた鋳造
性を有することから、流体機械やバルブなど形状が複雑
なものが多い産業機械器具材料としても広く用いられて
いる。さらに、ねずみ鋳鉄鋳物を長時間加熱したり加熱
冷却を繰り返したりすることによってこの鋳物を成長さ
せ、この成長によって生じた多孔質部（ポーラス部）に
潤滑油を含浸させることにより摺動性に優れた含油摺動
部材が得られることが知られており、この含油摺動部材
は軸受や滑り板などの摺動用途に広く用いられている。2. Description of the Related Art Gray cast iron in which carbon is present in the form of flake graphite has been known. Castings made from this gray cast iron (gray cast iron castings) are widely used as materials for internal combustion engines because of their large vibration absorption capacity and high thermal conductivity. Further, since gray cast iron has excellent castability, it is widely used as a material for industrial machinery, which often has complicated shapes such as fluid machinery and valves. Furthermore, by heating a gray cast iron casting for a long time or repeating heating and cooling, the casting is grown, and the porous portion (porous portion) generated by this growth is impregnated with lubricating oil, so that excellent slidability is achieved. It is known that an oil-impregnated sliding member can be obtained, and this oil-impregnated sliding member is widely used for sliding applications such as bearings and sliding plates.
【０００３】上述した各種用途に使用されるねずみ鋳鉄
鋳物は、荒引き加工、中引き加工、仕上げ加工、場合に
よっては研削加工などの機械加工を経て最終製品とな
る。ねずみ鋳鉄鋳物にこれらの機械加工を施す際には、
各加工工程で鋳鉄の切粉が生じる。このようにして生じ
た切粉の大部分は、通常、廃棄処分されている。The gray cast iron castings used for the above-mentioned various purposes are finished into a final product through mechanical processing such as roughing, intermediate drawing, finishing, and in some cases grinding. When performing these machining processes on gray cast iron castings,
Cast iron chips are generated in each processing step. Most of the chips produced in this way are usually discarded.
【０００４】廃棄処分されるねずみ鋳鉄鋳物の切粉に着
目し、この切粉を積極的に利用した技術として、例えば
特公昭５８−２１００２号公報に開示された技術が知ら
れている。この技術は、ねずみ鋳鉄の粉末（切屑）を４
トン／ｃｍ２以上の成形圧力で成形して成形品を得、そ
の後、鋳鉄に対して弱脱炭素性雰囲気もしくは中性雰囲
気であるアンモニア分解ガス雰囲気又はドライ水素雰囲
気において上記の成形品を少なくとも１０１０℃の温度
で焼結し、１０ｋｇ／ｍｍ２以上の引張り強さを有する
焼結成形体を製造する技術である。As a technique which pays attention to the chips of gray cast iron castings to be discarded and positively utilizes the chips, for example, the technique disclosed in Japanese Patent Publication No. 58-21002 is known. This technology produces 4 pieces of gray cast iron powder (chips).
A molded product is obtained by molding at a molding pressure of ton / cm 2 or more, and then the molded product is subjected to at least 1010 in a weak decarbonizing atmosphere or a neutral atmosphere, an ammonia decomposition gas atmosphere or a dry hydrogen atmosphere. This is a technique for producing a sintered compact having a tensile strength of 10 kg / mm 2 or more by sintering at a temperature of ° C.
【０００５】また、上記の切粉を使用して軸受などの摺
動用途の焼結成形体を製造する技術としては、例えば特
公昭５８−１２３２１号公報に開示された技術が知られ
ている。この技術は、鋳造品を切削又は研削して得られ
た切屑を粉砕することによりねずみ鋳鉄粉末を生成し、
このねずみ鋳鉄粉末９０重量％乃至９９．５重量％に炭
素粉末０．５重量％乃至１０重量％を混合して混合粉末
を作製し、この混合粉末を圧縮成形した後に焼結成形体
を製造する技術である。As a technique for producing a sintered compact for sliding use such as a bearing using the above chips, for example, a technique disclosed in Japanese Patent Publication No. 58-12321 is known. This technique produces gray cast iron powder by crushing chips obtained by cutting or grinding a cast product,
A technique for mixing 90% by weight to 99.5% by weight of the gray cast iron powder with 0.5% by weight to 10% by weight of carbon powder to prepare a mixed powder, and compression-molding the mixed powder, and then producing a sintered compact. Is.
【０００６】上述したように、特公昭５８−２１００２
号公報に開示された技術によれば、１０ｋｇ／ｍｍ２以
上の引張り強さを有する焼結成形体が製造されるので、
この技術（製造方法）で製造された焼結成形体は機械部
品として有効に利用され得るものである。しかし、この
焼結成形体には、潤滑性に寄与する遊離黒鉛の含有量が
少ないので、この焼結成形体は摩擦・摩耗等の摺動特性
に劣る。従って、この焼結成形体を軸受などの摺動用部
品として使用するに当たっては、潤滑条件や使用条件な
どを十分に注意しなければならない、という問題があ
る。As described above, Japanese Patent Publication No. 58-21002.
According to the technique disclosed in the publication, a sintered compact having a tensile strength of 10 kg / mm 2 or more is manufactured.
The sintered compact manufactured by this technique (manufacturing method) can be effectively used as a machine part. However, since the content of free graphite that contributes to lubricity is small in this sintered compact, this sintered compact is inferior in sliding characteristics such as friction and wear. Therefore, when using this sintered compact as a sliding component such as a bearing, there is a problem in that the lubrication conditions and usage conditions must be carefully considered.
【０００７】また、特公昭５８−１２３２１号公報に開
示された技術では、焼結成形体に潤滑性を付与する目的
で炭素粉末を含有している。しかし、この炭素粉末は焼
結性を阻害する原因となり、この結果、焼結成形体の強
度が弱いという欠点がある。このような欠点をもつ焼結
成形体は摺動用部品としては使用し難い、という問題が
ある。Further, in the technique disclosed in Japanese Patent Publication No. 58-12321, carbon powder is contained for the purpose of imparting lubricity to the sintered compact. However, this carbon powder becomes a cause of impairing sinterability, and as a result, there is a drawback that the strength of the sintered compact is weak. A sintered compact having such a drawback is difficult to use as a sliding component.
【０００８】[0008]
【発明が解決しようとする課題】上述した問題を解決す
るために、本願出願人は先に、特願２００１−６００２
号（以下「先行技術」という）において、摺動特性に優
れた鋳鉄系焼結摺動部材及びその製造方法を提案した。
この先行技術は、成長ねずみ鋳鉄鋳物を切削し、この切
削によって得られた切粉を所定の金型内に装填し、この
装填した切粉を３トン／ｃｍ２以上５トン／ｃｍ２以下
の範囲内の成形圧力で圧縮成形して圧粉体を形成し、中
性雰囲気または還元性雰囲気において１１００℃以上１
１５０℃以下の範囲の温度で３０分間以上９０分間以下
の時間内だけ前記圧粉体を焼結して鋳鉄系焼結摺動部材
を製造する方法である。この製造方法によって得られた
鋳鉄系焼結摺動部材は、遊離黒鉛が全体にわたって分散
含有されているので摩擦摩耗特性に優れており、軸受や
滑り板などの摺動用部品に適用できるものである。SUMMARY OF THE INVENTION In order to solve the above-mentioned problems, the applicant of the present invention has previously filed Japanese Patent Application No. 2001-6002.
No. 1 (hereinafter referred to as "prior art"), a cast iron-based sintered sliding member having excellent sliding characteristics and a method for manufacturing the same were proposed.
In this prior art, a grown gray cast iron casting is cut, and the cutting chips obtained by this cutting are loaded into a predetermined mold, and the loaded cutting chips of 3 tons / cm 2 or more and 5 tons / cm 2 or less are loaded. 1100 ° C. or higher in a neutral atmosphere or a reducing atmosphere by compression molding at a molding pressure within the range to form a green compact.
This is a method for producing a cast iron-based sintered sliding member by sintering the green compact at a temperature in the range of 150 ° C. or lower for a period of 30 minutes to 90 minutes. The cast iron-based sintered sliding member obtained by this production method has excellent friction and wear characteristics because free graphite is dispersed and contained throughout, and can be applied to sliding parts such as bearings and sliding plates. .
【０００９】本発明は、上記先行技術を有効に利用する
と共に、先行技術で得られた鋳鉄系焼結摺動部材の摩擦
摩耗特性をさらに向上させた鋳鉄系焼結摺動部材及びそ
の製造方法を提供することを目的とする。The present invention effectively utilizes the above-mentioned prior art, and further improves the friction and wear characteristics of the cast iron-based sintered sliding member obtained by the prior art and a method for producing the same. The purpose is to provide.
【００１０】[0010]
【課題を解決するための手段】上記目的を達成するため
の本発明の鋳鉄系焼結摺動部材は、（１）成長ねずみ鋳
鉄鋳物を切削することによって生じる切粉を焼結してな
る焼結合金を母材とし、この母材の少なくとも摺動表面
に四三酸化鉄の被膜が形成されていることを特徴とする
ものである。The cast iron-based sintered sliding member of the present invention for achieving the above object is (1) fired by sintering chips generated by cutting a grown gray cast iron casting. It is characterized in that a bond metal is used as a base material, and a coating of ferric tetroxide is formed on at least the sliding surface of the base material.
【００１１】ここで、（２）前記四三酸化鉄の被膜は、
２μｍ以上５μｍ以下の範囲内の厚さを有するものであ
ってもよい。Here, (2) the coating of ferric tetroxide is
It may have a thickness within the range of 2 μm or more and 5 μm or less.
【００１２】さらに、（３）前記四三酸化鉄の被膜は、
ビッカース硬さ（ＨｍＶ）が４４０以上５６０以下の範
囲内のものであってもよい。Further, (3) the coating of ferric tetroxide comprises:
The Vickers hardness (HmV) may be in the range of 440 or more and 560 or less.
【００１３】さらにまた、前記鋳鉄系焼結摺動部材は、
（４）その総体積の７体積％以上１５体積％以下の範囲
内の潤滑油が含有されているものであってもよい。Furthermore, the cast iron-based sintered sliding member is
(4) The lubricating oil may be contained in the range of 7% by volume or more and 15% by volume or less of the total volume.
【００１４】また、上記目的を達成するための本発明の
鋳鉄系焼結摺動部材の製造方法は、（５）成長ねずみ鋳
鉄鋳物を切削し、（６）この切削によって得られた切粉
を所定の金型内に装填し、（７）この装填した切粉を３
トン／ｃｍ２以上５トン／ｃｍ２以下の範囲内の成形圧
力で圧縮成形して圧粉体を形成し、（８）中性雰囲気ま
たは還元性雰囲気において１１００℃以上１１５０℃以
下の範囲内の温度で３０分間以上９０分間以下の時間内
だけ前記圧粉体を焼結して焼結合金母材を作製し、
（９）この焼結合金母材に水蒸気処理を施して少なくと
も摺動表面に四三酸化鉄の被膜を形成させて鋳鉄系焼結
摺動部材を製造することを特徴とするものである。Further, in the method for producing a cast iron-based sintered sliding member of the present invention for achieving the above object, (5) a grown gray cast iron casting is cut, and (6) cutting chips obtained by this cutting are cut. Load in a predetermined mold, (7) 3
(8) Within the range of 1100 ° C. or more and 1150 ° C. or less in a neutral atmosphere or a reducing atmosphere by compression molding with a molding pressure in the range of ton / cm 2 or more and 5 ton / cm 2 or less. A sintered alloy base material is produced by sintering the green compact at a temperature of 30 minutes or more and 90 minutes or less,
(9) A cast iron-based sintered sliding member is manufactured by subjecting this sintered alloy base material to steam treatment to form a coating of ferrosoferric oxide on at least the sliding surface.
【００１５】ここで、（１０）前記成長ねずみ鋳鉄鋳物
を得るに当たり、ねずみ鋳鉄鋳物のＡ１変態点よりも高
い温度とＡ１変態点よりも低い温度との間で加熱冷却を
繰り返す反覆加熱冷却処理をねずみ鋳鉄鋳物に施すこと
により前記成長ねずみ鋳鉄鋳物を得てもよい。(10) In obtaining the above-mentioned grown gray cast iron casting, heating and cooling are repeated between the temperature higher than the A 1 transformation point and the temperature lower than the A 1 transformation point of the gray cast iron casting. The grown gray cast iron casting may be obtained by subjecting a gray cast iron casting to a treatment.
【００１６】さらに、（１１）前記切粉を所定の金型内
に装填するに当たり、２０メッシュの篩を通過するが５
５メッシュの篩を通過しない切粉を総重量の８５重量％
以上９７重量％以下の範囲内で前記金型内に装填すると
共に、５５メッシュの篩を通過する切粉を総重量の３重
量％以上１５重量％以下の範囲内で前記金型内に装填し
てもよい。Further, (11) when loading the cutting chips into a predetermined die, the chips pass through a 20-mesh sieve, but 5
85% by weight of the total weight of chips that do not pass through a 5-mesh screen
It is loaded in the mold within the range of 97% by weight or more and the chips passing through the 55 mesh sieve are loaded in the mold within the range of 3% by weight to 15% by weight of the total weight. May be.
【００１７】さらにまた、（１２）２０メッシュの篩を
通過するが５５メッシュの篩を通過しない切粉を前記金
型内に装填するに当たり、該切粉の総重量のうち、１０
重量％以上９０重量％以下の範囲内であって２０メッシ
ュの篩を通過するが３６メッシュの篩を通過しない切粉
と、１０重量％以上９０重量％以下の範囲内であって３
６メッシュの篩を通過するが５５メッシュの篩を通過し
ない切粉とを混合して前記金型内に装填してもよい。Furthermore, (12) 10% of the total weight of the cutting chips is loaded into the mold when the cutting chips passing through the 20-mesh screen but not through the 55-mesh screen are loaded.
A chip that is in the range of not less than 90% by weight and passes through a sieve of 20 mesh, but does not pass through a sieve of 36 mesh, and is in the range of not less than 10% by weight and not more than 90% by weight.
Chips that pass through a 6-mesh screen but not through a 55-mesh screen may be mixed and loaded into the mold.
【００１８】さらにまた、（１３）前記水蒸気処理は、
処理温度が４５０℃以上５５０℃以下の範囲内であっ
て、６０分間以上９０分間以下の時間内で行ってもよ
い。Furthermore, (13) the steam treatment is
The treatment temperature may be in the range of 450 ° C. or higher and 550 ° C. or lower, and may be 60 minutes or longer and 90 minutes or shorter.
【００１９】さらにまた、（１４）前記鋳鉄系焼結摺動
部材に含油処理を施すに当たり、含油率が該鋳鉄系焼結
摺動部材の総体積の７体積％以上１５体積％以下の範囲
内になるように該鋳鉄系焼結摺動部材に含油処理を施し
てもよい。Furthermore, (14) when the cast iron-based sintered sliding member is subjected to oil impregnation, the oil content is within a range of 7% by volume to 15% by volume of the total volume of the cast iron-based sintered sliding member. The cast iron-based sintered sliding member may be subjected to oil impregnation treatment so that
【００２０】上記した四三酸化鉄の被膜について説明す
る。The coating of ferric tetroxide will be described.
【００２１】焼結摺動部材の観点からは、四三酸化鉄の
被膜は少なくとも焼結摺動部材の摺動表面に形成されて
いればよい。しかし、四三酸化鉄による防錆作用を考慮
した場合は、摺動部材の全ての表面に四三酸化鉄の被膜
を形成することが好ましく、これにより、摩擦摩耗特性
の向上に加えて焼結摺動部材に耐蝕性、耐錆性を付与で
きる。From the viewpoint of the sintered sliding member, the coating of ferric tetroxide may be formed on at least the sliding surface of the sintered sliding member. However, when considering the anticorrosive effect of ferric oxide, it is preferable to form a coating of ferric oxide on all surfaces of the sliding member, which improves the friction and wear characteristics and also the sintering. Corrosion resistance and rust resistance can be imparted to the sliding member.
【００２２】また、四三酸化鉄の被膜の厚さが２μｍ未
満の場合は、摺動特性、特に耐摩耗性の向上に効果が認
められにくい。一方、この被膜の厚さが5μｍを超えた
場合は、焼結合金母材の多孔部を封孔させる割合が多く
なり、焼結合金母材に含浸される潤滑油の含油率を低下
させるおそれがある。このような観点からは、四三酸化
鉄の被膜は、２μｍ以上５μｍ以下の範囲内の厚さを有
するものが好ましい。When the thickness of the ferrosoferric oxide film is less than 2 μm, it is difficult to recognize the effect of improving the sliding characteristics, especially the wear resistance. On the other hand, if the thickness of this coating exceeds 5 μm, the ratio of sealing the porous portion of the sintered alloy base material increases, which may reduce the oil content of the lubricating oil impregnated in the sintered alloy base material. There is. From such a point of view, it is preferable that the coating of ferrosoferric oxide has a thickness within the range of 2 μm or more and 5 μm or less.
【００２３】ところで、焼結合金母材の硬さを高めて耐
摩耗性を向上させる技術としては、例えば焼結合金母材
に焼入れを施し、表面硬さを高める技術が知られてい
る。しかし、この技術では、８００℃以上の高温で焼入
れをするので、焼結合金母材の組織に大きな変化をもた
らす。一方、水蒸気処理では、４５０以上５５０℃以下
の範囲で行われるので、焼結合金母材の組織に影響を及
ぼすことがなく、焼入れと同等の硬さを得ることができ
る。四三酸化鉄の被膜の表面硬さがビッカース硬さ（Ｈ
ｍＶ）４４０未満の場合は、耐摩耗性の向上に効果が認
められにくく、一方、四三酸化鉄の被膜の表面硬さがビ
ッカース硬さ５６０を超えた場合は相手材表面を損傷さ
せる虞がある。このような観点から、四三酸化鉄の被膜
の表面硬さはビッカース硬さ４５０以上５６０以下の範
囲内であることが好ましい。By the way, as a technique for increasing the hardness of the sintered alloy base material to improve the wear resistance, for example, a technique of increasing the surface hardness by quenching the sintered alloy base material is known. However, in this technique, since quenching is performed at a high temperature of 800 ° C. or higher, the structure of the sintered alloy base material is greatly changed. On the other hand, since the steam treatment is performed in the range of 450 to 550 ° C., it does not affect the structure of the sintered alloy base material, and the hardness equivalent to that of quenching can be obtained. The surface hardness of the ferrosoferric oxide coating is the Vickers hardness (H
mV) less than 440, it is difficult to recognize the effect of improving wear resistance. On the other hand, when the surface hardness of the triiron trioxide coating exceeds Vickers hardness 560, the surface of the mating material may be damaged. is there. From such a viewpoint, it is preferable that the surface hardness of the ferrosoferric oxide film is in the range of Vickers hardness of 450 or more and 560 or less.
【００２４】また、潤滑油を含有させるに際しては、周
知の加熱含浸法や真空含浸法を用いる。潤滑油として
は、エンジン油やマシン油などの鉱油を使用する。Further, when the lubricating oil is contained, the well-known heat impregnation method or vacuum impregnation method is used. Mineral oil such as engine oil or machine oil is used as the lubricating oil.
【００２５】[0025]
【発明の実施の形態】＜焼結合金母材の作製＞BEST MODE FOR CARRYING OUT THE INVENTION <Preparation of Sintered Alloy Base Material>
【００２６】炭素（Ｃ）２．５〜４．０重量％（２．５
重量％以上４．０重量％以下を表しており、以下同様で
ある）、珪素（Ｓｉ）０．５〜３．５重量％、マンガン
（Ｍｎ）０．２〜１．０重量％、燐（Ｐ）０．０３〜
０．８重量％、硫黄（Ｓ）０．０１〜０．１２重量％、
残部鉄（Ｆｅ）からなるねずみ鋳鉄鋳物に、このねずみ
鋳鉄鋳物のＡ１変態点（７２３℃）よりも高い温度とＡ
１変態点よりも低い温度との間で加熱冷却を繰り返す反
覆加熱冷却処理を施し、素地中の片状黒鉛を肥大成長さ
せた成長ねずみ鋳鉄鋳物を得る。成長ねずみ鋳鉄鋳物と
しては、素地がオールフェライト組織のものが好まし
い。ここで、素地がオールフェライト組織とは、素地が
フェライト組織だけからなることをいうが、フェライト
組織以外にパーライト組織など他の組織が僅かに存在す
る素地も、ここでいうオールフェライト組織に含まれ
る。Carbon (C) 2.5 to 4.0% by weight (2.5
% To 4.0% by weight, and the same applies hereinafter), silicon (Si) 0.5 to 3.5% by weight, manganese (Mn) 0.2 to 1.0% by weight, phosphorus ( P) 0.03-
0.8 wt%, sulfur (S) 0.01 to 0.12 wt%,
For a gray cast iron casting composed of the balance iron (Fe), a temperature higher than the A 1 transformation point (723 ° C.) of this gray cast iron casting and A
Repeated heating and cooling is repeated between heating and cooling at a temperature lower than one transformation point to obtain a grown gray cast iron casting in which flake graphite in the matrix is enlarged. As the grown gray cast iron casting, it is preferable that the substrate has an all-ferrite structure. Here, the all-ferrite structure as the base material means that the base material is composed only of the ferrite structure, but a base material in which other structures such as a pearlite structure are slightly present in addition to the ferrite structure is also included in the all-ferrite structure here. .
【００２７】この成長ねずみ鋳鉄鋳物に荒引き、中引き
及び仕上げの切削加工を施し、この成長ねずみ鋳鉄の切
粉を得る。このようにして得られた切粉の素地中には、
成長によって肥大化した片状黒鉛が多く含まれており、
これらの片状黒鉛が表面に露出している割合は多い。こ
の割合は、一般のねずみ鋳鉄鋳物を切削して得られた切
粉の表面に露出している片状黒鉛の割合よりも多い。This grown gray cast iron casting is subjected to roughing, medium drawing and finishing cutting to obtain chips of this grown gray cast iron. In the base material of the chips thus obtained,
It contains a large amount of flake graphite enlarged due to growth,
The rate at which these flake graphite is exposed on the surface is high. This proportion is higher than the proportion of flake graphite exposed on the surface of chips obtained by cutting a general gray cast iron casting.
【００２８】次に、切削加工の各工程で得られた切粉
を、２０メッシュの篩を通過するが５５メッシュの篩を
通過しない粒度の切粉と、５５メッシュの篩を通過する
粒度の切粉とに選別する。さらに、２０メッシュの篩を
通過するが５５メッシュの篩を通過しない粒度の切粉
を、２０メッシュの篩を通過するが３６メッシュの篩を
通過しない粒度の切粉と、３６メッシュを通過するが５
５メッシュの篩を通過しない粒度の切粉とに選別する。Next, the cutting chips obtained in each step of cutting are cut into particles having a particle size that passes through a 20-mesh screen but does not pass through a 55-mesh screen, and a cutting powder having a particle size that passes through a 55-mesh screen. Sort with powder. Further, the chips having a particle size that passes through the 20-mesh screen but does not pass through the 55-mesh screen, and the chips having the particle size that passes through the 20-mesh screen but does not pass through the 36-mesh screen and the 36-mesh screen 5
Sort into chips with a particle size that does not pass through a 5 mesh screen.
【００２９】上記のように選別した切粉のうち、２０メ
ッシュの篩を通過するが５５メッシュの篩を通過しない
粒度の切粉は主として焼結合金母材の骨格を形成する。
また、５５メッシュの篩を通過する粒度の切粉では、切
粉中に占める黒鉛量が多い。従って、５５メッシュの篩
を通過する切粉を焼結合金母材全体に分散して含有させ
ることにより、この焼結合金母材は、黒鉛等の潤滑性成
分を別途に含有させなくても、潤滑作用を発揮する。Among the chips selected as described above, the chips having a particle size that passes through the 20-mesh sieve but does not pass through the 55-mesh sieve mainly form the skeleton of the sintered alloy base material.
In addition, in the case of chips having a particle size that passes through a 55-mesh screen, the amount of graphite in the chips is large. Therefore, by allowing the chips passing through the 55-mesh sieve to be dispersed and contained in the entire sintered alloy base material, the sintered alloy base material does not need to contain a lubricating component such as graphite separately, Exhibits a lubricating effect.
【００３０】選別した各粒度の切粉のうち、２０メッシ
ュの篩を通過するが５５メッシュの篩を通過しない粒度
の切粉８５〜９７重量％と、５５メッシュの篩を通過す
る粒度の切粉３〜１５重量％とを混合して混合粉末を作
製する。ここでは、２０メッシュの篩を通過するが５５
メッシュの篩を通過しない粒度の切粉のうち、２０メッ
シュの篩を通過するが３６メッシュの篩を通過しない粒
度の切粉１０〜９０重量％と、３６メッシュを通過する
が５５メッシュの篩を通過しない粒度の切粉１０〜９０
重量％とを混合した切粉８５〜９７重量％に対し、５５
メッシュの篩を通過する粒度の切粉３〜１５重量％を混
合した混合粉末になるように作製する。なお、各切粉の
重量％は、作製した混合粉末の総重量に対する割合であ
る。Of the selected cutting chips of each particle size, 85 to 97% by weight of cutting particles having a particle size that passes through a 20-mesh sieve but does not pass through a 55-mesh screen, and a cutting particle having a particle size that passes through a 55-mesh screen. 3 to 15% by weight is mixed to prepare a mixed powder. Here, it passes through a 20 mesh screen,
Among the chips having a particle size that does not pass through a mesh screen, 10 to 90% by weight of a chip having a particle size that passes through a 20-mesh screen but does not pass through a 36-mesh screen, and a 55-mesh screen that passes through 36-mesh 10 to 90 chips with particle size that does not pass
55 to 95% by weight of chips mixed with 50% by weight,
A mixed powder is prepared by mixing 3 to 15% by weight of cutting powder having a particle size that passes through a mesh sieve. The weight% of each cutting powder is the ratio to the total weight of the produced mixed powder.
【００３１】このようにして得た混合粉末を金型中に装
填し、３トン／ｃｍ２以上５トン／ｃｍ２以下の範囲内
の成形圧力で圧縮成形して圧粉体を作製する。この圧粉
体を、中性雰囲気または還元性雰囲気において１１００
℃以上１１５０℃以下の範囲内の温度で３０分間以上９
０分間以下の範囲内の時間だけ焼結して焼結合金母材を
作製する。The mixed powder thus obtained is loaded into a mold and compression molded at a molding pressure within the range of 3 tons / cm 2 to 5 tons / cm 2 to produce a green compact. This green compact is treated with 1100 in a neutral or reducing atmosphere.
30 minutes or more at a temperature within the range of ℃ to 1150 ℃
A sintered alloy base material is produced by sintering for a time within a range of 0 minutes or less.
【００３２】＜鋳鉄系焼結摺動部材の製造＞<Production of Cast Iron Sintered Sliding Member>
【００３３】上記のようにして得た焼結合金母材を加熱
炉内に置き、加熱炉内の温度を４５０℃以上５５０℃以
下の範囲内に昇温して、この温度を保持した状態で加熱
炉内に水蒸気を６０分間以上９０分間以下の時間内で連
続して噴射して焼結合金母材に水蒸気処理を施す。この
水蒸気処理により、焼結合金母材の摺動表面に２μｍ以
上５μｍ以下の範囲内の厚さであって、ビッカース硬さ
が４４０以上５６０以下の範囲内の四三酸化鉄の被膜を
形成させる。水蒸気処理を施すに当たり、処理温度及び
処理時間は、焼結合金母材の摺動表面に形成される四三
酸化鉄の被膜の巧拙（被膜が一様な厚さを有するか否
か）、焼結合金母材に含有されている遊離炭素（黒鉛）
の脱炭、多孔部の封孔等に影響を及ぼすので重要な要素
となる。このようにして、少なくとも摺動表面に四三酸
化鉄の被膜が形成された鋳鉄系焼結摺動部材が製造され
る。The sintered alloy base material obtained as described above is placed in a heating furnace, the temperature in the heating furnace is raised to a range of 450 ° C. or higher and 550 ° C. or lower, and the temperature is maintained. Steam is continuously injected into the heating furnace for 60 minutes or more and 90 minutes or less to subject the sintered alloy base material to steam treatment. By this steam treatment, a coating of ferric tetroxide having a thickness in the range of 2 μm or more and 5 μm or less and a Vickers hardness of 440 or more and 560 or less is formed on the sliding surface of the sintered alloy base material. . In carrying out the steam treatment, the treatment temperature and treatment time are determined by the skill of the coating of ferrosoferric oxide formed on the sliding surface of the sintered alloy base material (whether or not the coating has a uniform thickness), the firing. Free carbon (graphite) contained in the bonded gold matrix
It is an important factor because it affects the decarburization of, the sealing of porous parts, etc. In this way, a cast iron-based sintered sliding member having a coating of ferrosoferric oxide formed on at least the sliding surface is manufactured.
【００３４】上記鋳鉄系焼結摺動部材に含油処理を施す
ことにより、７体積％以上１５体積％以下の含油率の鋳
鉄系含油焼結摺動部材が得られる。従って、鋳鉄系含油
焼結摺動部材には、７体積％以上１５体積％以下の範囲
内の潤滑油が含有されていることとなる。By subjecting the cast iron-based sintered sliding member to oil impregnation, a cast iron-based oil impregnated sintered sliding member having an oil content of 7% by volume or more and 15% by volume or less can be obtained. Therefore, the cast iron-based oil-impregnated sintered sliding member contains the lubricating oil in the range of 7% by volume or more and 15% by volume or less.
【００３５】この鋳鉄系焼結摺動部材には、少なくとも
摺動表面には四三酸化鉄の硬質な被膜と、遊離黒鉛と、
多孔部及び遊離黒鉛に含有された潤滑油とが存在するの
で、相手材との摺動においては、先行技術において提案
した鋳鉄系焼結摺動部材に比較して、摩擦摩耗特性の大
幅な向上を図ることができる。In this cast iron-based sintered sliding member, a hard coating of ferric tetroxide and free graphite are provided on at least the sliding surface.
Since there is a lubricating oil contained in the porous part and free graphite, in sliding with the mating material, the friction and wear characteristics are greatly improved compared to the cast iron type sintered sliding member proposed in the prior art. Can be achieved.
【００３６】[0036]
【実施例】以下、本発明の実施例について詳細に説明す
る。本発明はこれらの例に何等限定されるものではな
い。EXAMPLES Examples of the present invention will be described in detail below. The invention is in no way limited to these examples.
【００３７】〔実施例１〕[Example 1]
【００３８】３．６５重量％の炭素（Ｃ）、２．２２重
量％の珪素（Ｓｉ）、０．４５重量％のマンガン（Ｍ
ｎ）、０．０４５重量％の燐（Ｐ）、０．０８４重量％
の硫黄（Ｓ）、残部鉄（Ｆｅ）からなる組成を有し、内
径３３ｍｍ、外径５４ｍｍ、長さ２０３ｍｍの円筒状ね
ずみ鋳鉄鋳物（ＦＣ１５０）を作製した。このねずみ鋳
鉄鋳物のＡ１変態点（７２３℃）よりも高い温度と低い
温度との間で加熱冷却を繰り返す（Ａ１変態点をはさん
で上下する）反復加熱冷却処理によって、ねずみ鋳鉄素
地中の片状黒鉛を肥大成長させると共に、この成長に伴
い片状黒鉛の周囲を多孔質化させた。このようにして成
長ねずみ鋳鉄鋳物を得た。3.65 wt% carbon (C), 2.22 wt% silicon (Si), 0.45 wt% manganese (M
n), 0.045 wt% phosphorus (P), 0.084 wt%
A cylindrical gray cast iron casting (FC150) having a composition of sulfur (S) and balance iron (Fe), having an inner diameter of 33 mm, an outer diameter of 54 mm, and a length of 203 mm was produced. By repeatedly heating and cooling between a temperature higher and lower than the A 1 transformation point (723 ° C.) of this gray cast iron casting (it goes up and down across the A 1 transformation point), in the gray cast iron substrate The flake graphite of No. 1 was enlarged and the periphery of the flake graphite was made porous along with this growth. In this way, a grown gray cast iron casting was obtained.
【００３９】上記の成長ねずみ鋳鉄鋳物の表面に生成し
た酸化スケールを除去し、その後、この成長ねずみ鋳鉄
鋳物に荒引き、中引き及び仕上げの切削加工を施し、内
径４０ｍｍ、外径５０ｍｍ、長さ４０ｍｍの軸受ブッシ
ュを作製した。このようにして成長ねずみ鋳鉄鋳物を切
削加工して軸受ブッシュを作製する際に多量の切粉が生
じた。これら多量の切粉を、２０メッシュの篩を通過す
るが５５メッシュの篩を通過しない切粉と、５５メッシ
ュの篩を通過する切粉とに選別した。Oxide scale formed on the surface of the above-mentioned grown gray cast iron casting is removed, and thereafter, this grown gray cast iron casting is subjected to roughing, medium-drawing and finishing cutting work to obtain an inner diameter of 40 mm, an outer diameter of 50 mm and a length. A 40 mm bearing bush was produced. In this way, a large amount of chips were produced when the grown gray cast iron casting was cut to produce a bearing bush. These large amounts of chips were sorted into chips that passed through a 20-mesh screen but did not pass through a 55-mesh screen and chips that passed through a 55-mesh screen.
【００４０】さらに、２０メッシュの篩を通過するが５
５メッシュの篩を通過しない切粉を、２０メッシュの篩
を通過するが３６メッシュの篩を通過しない切粉と、３
６メッシュの篩を通過するが５５メッシュの篩を通過し
ない切粉とに選別した。Further, though passing through a 20-mesh screen,
Chips that do not pass through a 5-mesh screen, and chips that pass through a 20-mesh screen but do not pass through a 36-mesh screen, and 3
It was sorted into chips that passed through a 6-mesh screen but did not pass through a 55-mesh screen.
【００４１】上記のように選別した各粒度の切粉の中か
ら、２０メッシュの篩を通過するが３６メッシュの篩を
通過しない切粉を総重量の５６重量％、３６メッシュの
篩を通過するが５５メッシュの篩を通過しない切粉を総
重量の３６重量％、５５メッシュの篩を通過する切粉を
総重量の８重量％、それぞれ計量した。各切粉の組成を
表１に示す。Among the chips of each particle size selected as described above, the chips passing through the 20-mesh sieve but not through the 36-mesh sieve are passed through the 36-mesh sieve at 56% by weight of the total weight. Of the powder which did not pass through the 55 mesh screen was weighed in an amount of 36% by weight based on the total weight, and the powder which passed through the 55 mesh screen was measured in an amount of 8% by weight based on the total weight. The composition of each chip is shown in Table 1.
【表１】 [Table 1]
【００４２】表１において、−２０メッシュは、２０メ
ッシュの篩を通過することを表し、＋５５メッシュは、
５５メッシュの篩を通過しないことを表す。なお、以下
の各表においても同様である。In Table 1, -20 mesh means passing through a 20 mesh screen, and +55 mesh is
It means that it does not pass through a 55 mesh screen. The same applies to the following tables.
【００４３】上記のようにして選別し計量した各切粉を
混合して混合粉末を作製した。ついで、この混合粉末を
直方体状の中空部を有する金型内に装填し、成形圧力４
トン／ｃｍ２で圧縮成形して圧粉体を作製した。その
後、水素ガス雰囲気（本発明にいう中性雰囲気または還
元性雰囲気の一例である）に調整した加熱炉において、
この圧粉体を１１３０℃の温度で６０分間焼結し、直方
体状の焼結体を得た。このようにして得た焼結体を切削
加工して、一辺が３０ｍｍ、厚さ５ｍｍの横断面正方形
状の焼結合金母材を作製した。Chips selected and weighed as described above were mixed to prepare a mixed powder. Then, this mixed powder is loaded into a mold having a rectangular parallelepiped hollow portion, and a molding pressure of 4
A green compact was produced by compression molding at ton / cm 2 . Then, in a heating furnace adjusted to a hydrogen gas atmosphere (which is an example of a neutral atmosphere or a reducing atmosphere according to the present invention),
The green compact was sintered at a temperature of 1130 ° C. for 60 minutes to obtain a rectangular parallelepiped sintered body. The sintered body thus obtained was cut to produce a sintered alloy base material having a square cross section with a side of 30 mm and a thickness of 5 mm.
【００４４】ついで、焼結合金母材を加熱炉内に置き、
加熱炉内の温度を４８０℃に昇温した後、この温度を保
持した状態で加熱炉内に水蒸気を９０分間連続して噴射
し、焼結合金母材に水蒸気処理を施した。この水蒸気処
理により、焼結合金母材の表面に厚さ３μｍの四三酸化
鉄の被膜が形成された鋳鉄系焼結摺動部材を得た。四三
酸化鉄の被膜はビッカース硬さ（ＨｍＶ）４４２であっ
た。また、この鋳鉄系焼結摺動部材に含油処理を施した
ところ、潤滑油の含油率は１０．３体積％であった。Then, the sintered alloy base material is placed in a heating furnace,
After the temperature inside the heating furnace was raised to 480 ° C., steam was continuously injected into the heating furnace for 90 minutes while maintaining this temperature to subject the sintered alloy base material to steam treatment. By this steam treatment, a cast iron-based sintered sliding member having a 3 μm thick ferrosoferric oxide film formed on the surface of the sintered alloy base material was obtained. The coating of ferric tetroxide had a Vickers hardness (HmV) of 442. When this cast iron-based sintered sliding member was subjected to an oil impregnation treatment, the oil content of the lubricating oil was 10.3% by volume.
【００４５】〔実施例２〕[Example 2]
【００４６】上記した実施例１と同様にして、成長ねず
み鋳鉄鋳物を切削加工して軸受ブッシュを作製する際に
生じた切粉を、２０メッシュの篩を通過するが５５メッ
シュの篩を通過しない切粉と、５５メッシュの篩を通過
する切粉とに選別した。In the same manner as in Example 1 described above, the chips produced when the grown gray cast iron casting is cut to form a bearing bush pass through a 20-mesh sieve but not a 55-mesh sieve. The chips were classified into chips and chips passing through a 55-mesh screen.
【００４７】さらに、２０メッシュの篩を通過するが５
５メッシュの篩を通過しない切粉を、２０メッシュの篩
を通過するが３６メッシュの篩を通過しない切粉と、３
６メッシュの篩を通過するが５５メッシュの篩を通過し
ない切粉とに選別した。このようにして選別した各粒度
の切粉の中から、２０メッシュの篩を通過するが３６メ
ッシュの篩を通過しない切粉を総重量の３０重量％、３
６メッシュの篩を通過するが５５メッシュの篩を通過し
ない切粉を総重量の６０重量％、５５メッシュの篩を通
過する切粉を総重量の１０重量％、それぞれ計量した。
各切粉の組成を表２に示す。After passing through a 20-mesh screen,
Chips that do not pass through a 5-mesh screen, and chips that pass through a 20-mesh screen but do not pass through a 36-mesh screen, and 3
It was sorted into chips that passed through a 6-mesh screen but did not pass through a 55-mesh screen. Among the chips of each particle size selected in this manner, 30% by weight of the total weight of chips that pass through a 20-mesh sieve but not a 36-mesh sieve are used.
Chips passing through a 6-mesh screen but not through a 55-mesh screen were weighed in an amount of 60% by weight based on the total weight, and chips passing through a 55-mesh screen in an amount of 10% by weight based on the total weight.
Table 2 shows the composition of each chip.
【表２】 [Table 2]
【００４８】上記のようにして選別し計量した各切粉を
混合して混合粉末を形成した。ついで、この混合粉末を
直方体状の中空部を有する金型内に装填し、成形圧力４
トン／ｃｍ２で圧縮成形して圧粉体を作製した。その
後、実施例１と同様に、水素ガス雰囲気に調整した加熱
炉において、この圧粉体を１１３０℃の温度で６０分間
焼結し、直方体状の焼結体を得た。このようにして得た
焼結体を切削加工して、一辺が３０ｍｍ、厚さ５ｍｍの
横断面正方形状の焼結合金母材を作製した。The respective chips that were selected and weighed as described above were mixed to form a mixed powder. Then, this mixed powder is loaded into a mold having a rectangular parallelepiped hollow portion, and a molding pressure of 4
A green compact was produced by compression molding at ton / cm 2 . Then, in the same manner as in Example 1, in a heating furnace adjusted to a hydrogen gas atmosphere, the green compact was sintered at a temperature of 1130 ° C. for 60 minutes to obtain a rectangular parallelepiped sintered body. The sintered body thus obtained was cut to produce a sintered alloy base material having a square cross section with a side of 30 mm and a thickness of 5 mm.
【００４９】ついで、焼結合金母材を加熱炉内に置き、
加熱炉内の温度を５５０℃に昇温した後、この温度を保
持した状態で加熱炉内に水蒸気を６０分間連続して噴射
し、焼結合金母材に水蒸気処理を施した。この水蒸気処
理により、焼結合金母材の表面に厚さ５μｍの四三酸化
鉄の被膜が形成された鋳鉄系焼結摺動部材を得た。四三
酸化鉄の被膜はビッカース硬さ（ＨｍＶ）５０３であっ
た。また、この鋳鉄系焼結摺動部材に含油処理を施した
ところ、潤滑油の含油率は９．６体積％であった。Then, the sintered alloy base material is placed in a heating furnace,
After the temperature inside the heating furnace was raised to 550 ° C., steam was continuously injected into the heating furnace for 60 minutes while maintaining this temperature, and the sintered alloy base material was subjected to steam treatment. By this steam treatment, a cast iron-based sintered sliding member having a 5 μm thick coating of ferric tetroxide on the surface of the sintered alloy base material was obtained. The coating of ferric tetroxide had a Vickers hardness (HmV) of 503. When this cast iron-based sintered sliding member was subjected to an oil impregnation treatment, the oil content of the lubricating oil was 9.6% by volume.
【００５０】〔比較例１〕Comparative Example 1
【００５１】３．６５重量％のＣ、２．２２重量％のＳ
ｉ、０．４５重量％のＭｎ、０．０４５重量％のＰ、
０．０８４重量％のＳ、残部Ｆｅからなり、内径３３ｍ
ｍ、外径５４ｍｍ、長さ２０３ｍｍの円筒状ねずみ鋳鉄
鋳物（ＦＣ１５０）を作製した。このねずみ鋳鉄鋳物に
荒引き、中引き及び仕上げの各切削加工を施し、内径４
０ｍｍ、外径５０ｍｍ、長さ４０ｍｍの軸受ブッシュを
作製した。このようにしてねずみ鋳鉄鋳物を切削加工し
て軸受ブッシュを作製する際には多量の切粉が生じた。
これら多量の切粉を、２０メッシュの篩を通過するが５
５メッシュの篩を通過しない粒度の切粉と、５５メッシ
ュの篩を通過する粒度の切粉とに選別した。3.65% by weight C, 2.22% by weight S
i, 0.45 wt% Mn, 0.045 wt% P,
0.084 wt% S, balance Fe
A cylindrical gray cast iron casting (FC150) having m, an outer diameter of 54 mm and a length of 203 mm was produced. This gray cast iron casting is subjected to roughing, medium-drawing and finishing cutting operations, and an inner diameter of 4
A bearing bush having a diameter of 0 mm, an outer diameter of 50 mm and a length of 40 mm was manufactured. In this way, a large amount of chips were generated when the bearing bush was manufactured by cutting the gray cast iron casting.
Although a large amount of these chips pass through a 20-mesh screen,
The chips having a particle size not passing through a 5 mesh screen and the chips having a particle size passing through a 55 mesh screen were selected.
【００５２】さらに、２０メッシュの篩を通過するが５
５メッシュの篩を通過しない粒度の切粉を、２０メッシ
ュの篩を通過するが３６メッシュの篩を通過しない粒度
の切粉と、３６メッシュの篩を通過するが５５メッシュ
の篩を通過しない粒度の切粉とに選別した。Further, though passing through a 20-mesh sieve,
Chips with a particle size that does not pass through a 5-mesh screen pass through a 20-mesh screen but do not pass through a 36-mesh screen, and particle sizes that pass through a 36-mesh screen but do not pass through a 55-mesh screen. It was sorted into chips and.
【００５３】上記のように選別した各粒度の切粉の中か
ら、２０メッシュの篩を通過するが３６メッシュの篩を
通過しない粒度の切粉を総重量の５６重量％、３６メッ
シュの篩を通過するが５５メッシュの篩を通過しない粒
度の切粉を総重量の３６重量％、５５メッシュの篩を通
過する粒度の切粉を総重量の８重量％、それぞれ計量し
た。各切粉の組成を表３に示す。Among the chips of each particle size selected as described above, 56% by weight of the total weight of chips having a particle size that passes through a 20-mesh sieve but does not pass through a 36-mesh screen, and a 36-mesh screen is used. 36% by weight of the chips having a particle size that passed through the 55-mesh sieve and 8% by weight of the particles having a particle size that passed through the 55-mesh sieve were weighed. Table 3 shows the composition of each chip.
【表３】 [Table 3]
【００５４】上記のように選別し計量した各切粉を混合
して混合粉末を形成した。ついで、この混合粉末を直方
体状の中空部を有する金型内に装填し、成形圧力４トン
／ｃｍ２で圧縮成形して圧粉体を作製した。その後、加
熱炉において、この圧粉体を１１３０℃の温度で６０分
間焼結して焼結体を得た。この焼結体を切削加工して、
一辺が３０ｍｍ、厚さ５ｍｍの横断面正方形状の焼結摺
動部材を製造した。この鋳鉄系焼結摺動部材に含油処理
を施したところ、潤滑油の含油率は１２．３体積％であ
った。The respective chips that were selected and weighed as described above were mixed to form a mixed powder. Next, this mixed powder was loaded into a mold having a rectangular parallelepiped hollow portion, and compression molded at a molding pressure of 4 ton / cm 2 to prepare a green compact. Then, in a heating furnace, the green compact was sintered at a temperature of 1130 ° C. for 60 minutes to obtain a sintered body. By cutting this sintered body,
A sintered sliding member having a square cross section with a side of 30 mm and a thickness of 5 mm was manufactured. When this cast iron-based sintered sliding member was subjected to oil impregnation treatment, the oil content of the lubricating oil was 12.3% by volume.
【００５５】〔比較例２〕[Comparative Example 2]
【００５６】実施例１と同様の成分組成であって、同様
の粒度分布の切粉を使用し、かつ同様の条件で焼結した
一辺が３０ｍｍ、厚さ５ｍｍの横断面正方形状の焼結合
金母材を焼結摺動部材とした。この鋳鉄系焼結摺動部材
に含油処理を施したところ、潤滑油の含油率は１２．２
体積％であった。この比較例２の焼結摺動部材は、上記
した先行技術の焼結摺動部材に相当するものである。Sintered alloy having the same composition as in Example 1 and using chips having the same particle size distribution, and sintered under the same conditions and having a square cross section with a side of 30 mm and a thickness of 5 mm. The base material was a sintered sliding member. When this cast iron-based sintered sliding member was subjected to oil impregnation treatment, the oil content of the lubricating oil was 12.2.
It was% by volume. The sintered sliding member of Comparative Example 2 corresponds to the above-mentioned sintered sliding member of the prior art.
【００５７】つぎに、上記した実施例１、実施例２、比
較例１、及び比較例２で得た焼結摺動部材について、下
記に示す試験条件により耐荷重試験を行った。Next, load bearing tests were carried out on the sintered sliding members obtained in the above-mentioned Examples 1, 2 and Comparative Examples 1 and 2 under the test conditions shown below.
【００５８】〔耐荷重試験〕
試験条件
すべり速度 ：３ｍ／ｍｉｎ
荷重（面圧）：１０分間毎に３０ｋｇｆ／ｃｍ２の荷重
（面圧）を累積負荷した。
相手材 ：機械構造用炭素鋼（Ｓ４５Ｃ）
試験方法 ：スラスト試験で行い、摩擦係数が０．３
に達した時点で試験を中止した。
潤滑方法 ：試験開始時に摺動面にグリースを塗布し
た。[Withstand load test] Test conditions Sliding speed: 3 m / min Load (contact pressure): A load (contact pressure) of 30 kgf / cm 2 was cumulatively applied every 10 minutes. Counterpart material: Carbon steel for machine structure (S45C) Test method: Thrust test, friction coefficient 0.3
The test was discontinued at the time of reaching. Lubrication method: Grease was applied to the sliding surface at the start of the test.
【００５９】この耐荷重試験の結果を図１に示す。図１
は、累積荷重（面圧）と摩擦係数の推移を示したグラフ
であり、縦軸は摩擦係数を表し、横軸は累積荷重（面
圧）を表す。The results of this load bearing test are shown in FIG. Figure 1
Is a graph showing changes in cumulative load (surface pressure) and friction coefficient, the vertical axis represents the friction coefficient, and the horizontal axis represents the cumulative load (surface pressure).
【００６０】図１に示すように、比較例１の摺動部材で
は、試験開始から比較的安定した摩擦係数で推移した
が、累積荷重が９０ｋｇｆ／ｃｍ２を超えると摩擦係数
が徐々に上昇し、累積荷重１８０ｋｇｆ／ｃｍ２で摩擦
係数が０．３に達したので試験を中止した。比較例１の
焼結摺動部材が累積荷重１８０ｋｇｆ／ｃｍ２で異常摩
耗に移行した理由は、この焼結摺動部材に含有されてい
る潤滑油が枯渇したからである、と推察される。As shown in FIG. 1, in the sliding member of Comparative Example 1, the friction coefficient remained relatively stable from the start of the test, but when the cumulative load exceeded 90 kgf / cm 2 , the friction coefficient gradually increased. Since the friction coefficient reached 0.3 at a cumulative load of 180 kgf / cm 2 , the test was stopped. It is speculated that the reason why the sintered sliding member of Comparative Example 1 shifted to abnormal wear at a cumulative load of 180 kgf / cm 2 was that the lubricating oil contained in this sintered sliding member was exhausted.
【００６１】また、比較例２の焼結摺動部材は、試験開
始から徐々に摩擦係数が低下し、累積荷重が２１０ｋｇ
ｆ／ｃｍ２を超えるあたりから摩擦係数が徐々に上昇し
始め、累積荷重が３３０ｋｇｆ／ｃｍ２で摩擦係数が
０．３に達したので試験を中止した。この比較例２の焼
結摺動部材について、試験後、相手材の表面を観察した
ところ、この焼結摺動部材に含有されている遊離黒鉛の
潤滑被膜が相手材の表面に形成されていることが確認さ
れた。比較例２の焼結摺動部材が比較例１の焼結摺動部
材よりも耐荷重性に優れている理由は、比較例２の焼結
摺動部材に含有されている遊離黒鉛は、比較例１の焼結
摺動部材のそれよりも多く、この遊離黒鉛の潤滑作用と
焼結摺動部材に含有された潤滑油の潤滑作用とが相俟っ
て発揮されたからである、と推察される。In the sintered sliding member of Comparative Example 2, the friction coefficient gradually decreased from the start of the test, and the cumulative load was 210 kg.
The friction coefficient began to gradually increase from around f / cm 2 , and the cumulative load reached 330 kgf / cm 2 , and the friction coefficient reached 0.3, so the test was stopped. After the test, the surface of the mating material of the sintered sliding member of Comparative Example 2 was observed. As a result, a lubricating coating of free graphite contained in the mating material was formed on the surface of the mating material. It was confirmed. The reason why the sintered sliding member of Comparative Example 2 is superior in load bearing capacity to the sintered sliding member of Comparative Example 1 is that the free graphite contained in the sintered sliding member of Comparative Example 2 is It is presumed that this is because it was more than that of the sintered sliding member of Example 1, and the lubricating action of this free graphite and the lubricating action of the lubricating oil contained in the sintered sliding member were exhibited together. It
【００６２】一方、実施例１及び実施例２の焼結摺動部
材は、試験開始から累積荷重が４８０ｋｇｆ／ｃｍ２ま
で摩擦係数が０．１５以下と安定した値を示した。この
耐荷重試験の結果から、実施例１及び実施例２の焼結摺
動部材は比較例２の焼結摺動部材の１．６倍の耐荷重性
能を有するものであることがわかる。On the other hand, the sintered sliding members of Examples 1 and 2 showed a stable coefficient of friction of 0.15 or less from the start of the test to the cumulative load of 480 kgf / cm 2 . From the results of this load bearing test, it is understood that the sintered sliding members of Examples 1 and 2 have load bearing performance 1.6 times that of the sintered sliding member of Comparative Example 2.
【００６３】つぎに、上記した耐荷重試験の結果を踏ま
え、実施例１、実施例２、及び比較例２の焼結摺動部材
について下記に示す試験条件により耐久試験を行い、耐
摩耗性を比較した。試験結果を表４に示す。Next, based on the results of the load resistance test described above, the sintered sliding members of Examples 1, 2 and Comparative Example 2 were subjected to a durability test under the test conditions shown below to show wear resistance. Compared. The test results are shown in Table 4.
【００６４】〔耐久試験〕[Durability Test]
【００６５】＜試験条件１＞
すべり速度 ：５ｍ／ｍｉｎ
荷重（面圧）：１００ｋｇｆ／ｃｍ２
試験時間 ：１０ｈｒ
相手材 ：機械構造用炭素鋼（Ｓ４５Ｃ）
試験方法 ：スラスト試験
潤滑方法 ：試験開始時に摺動面にグリースを塗布し
た。<Test condition 1> Sliding speed: 5 m / min Load (contact pressure): 100 kgf / cm 2 Test time: 10 hr Counterpart material: Carbon steel for machine structure (S45C) Test method: Thrust test Lubrication method: At the start of test Grease was applied to the sliding surface.
【００６６】＜試験条件２＞
すべり速度 ：３ｍ／ｍｉｎ
荷重（面圧）：２５０ｋｇｆ／ｃｍ２
試験時間 ：１０ｈｒ
相手材 ：機械構造用炭素鋼（Ｓ４５Ｃ）
試験方法 ：スラスト試験
潤滑方法 ：試験開始時に摺動面にグリースを塗布し
た。<Test condition 2> Slip velocity: 3 m / min Load (contact pressure): 250 kgf / cm 2 Test time: 10 hr Counterpart material: Carbon steel for machine structure (S45C) Test method: Thrust test Lubrication method: At the start of the test Grease was applied to the sliding surface.
【表４】 [Table 4]
【００６７】表４における実施例１、実施例２及び比較
例２の摺動部材の摩耗量とは、各実施例及び比較例の焼
結摺動部材の厚さ５ｍｍが耐久試験によって減少したと
きの減少量をいう。相手材の摩耗量も同様である。The wear amounts of the sliding members of Example 1, Example 2 and Comparative Example 2 in Table 4 are the values when the thickness of 5 mm of the sintered sliding members of each Example and Comparative Example was decreased by the durability test. The decrease amount of The amount of wear of the mating material is the same.
【００６８】耐久試験条件１においては、実施例１、実
施例２及び比較例２の焼結摺動部材の摩耗量は極めて少
なく、特に実施例１及び実施例２双方の焼結摺動部材の
摩耗量は零であった。一方、耐久試験条件２において
は、実施例１及び実施例２双方の焼結摺動部材の摩耗量
は極めて少なかった。これに対し、比較例２の焼結摺動
部材は試験開始後３０分で異常摩耗を起こしたので摩耗
量の測定はできず、表４にはその摩耗量が記載されてい
ない。Under the durability test condition 1, the amount of wear of the sintered sliding members of Examples 1, 2 and Comparative Example 2 was extremely small. The amount of wear was zero. On the other hand, under the durability test condition 2, the wear amount of the sintered sliding members of both Example 1 and Example 2 was extremely small. On the other hand, the sintered sliding member of Comparative Example 2 suffered abnormal wear after 30 minutes from the start of the test, so the amount of wear could not be measured, and Table 4 does not show the amount of wear.
【００６９】以上の耐荷重試験及び耐久試験の結果か
ら、実施例１及び実施例２の焼結摺動部材では、その摺
動表面に、四三酸化鉄の硬質の被膜と、遊離黒鉛と、多
孔部及び遊離黒鉛に含有された潤滑油とが存在し、且
つ、潤滑油剤（グリース）が介在しているので、相手材
との摺動の際に低い摩擦係数で安定して摺動して摩耗量
も極めて少ない、ことが判明した。従って、実施例１及
び実施例２の焼結摺動部材は、その使用条件によっては
従来技術及び先行技術の使用条件を大幅に上回り、使用
範囲が大幅に拡大されることとなる。From the results of the load bearing test and the durability test, the sintered sliding members of Examples 1 and 2 had a hard coating of ferric tetroxide and free graphite on the sliding surface. Since there is a lubricating oil contained in the porous part and free graphite, and a lubricating oil (grease) is present, it is possible to slide stably with a low friction coefficient when sliding with the mating material. It was found that the amount of wear was also extremely small. Therefore, the sintered sliding members of Example 1 and Example 2 greatly exceed the usage conditions of the prior art and the prior art depending on the usage conditions, and the usage range is greatly expanded.
【００７０】[0070]
【発明の効果】以上説明したように本発明の鋳鉄系焼結
摺動部材は、成長ねずみ鋳鉄鋳物を切削することによっ
て生じる切粉を焼結してなる焼結合金母材の少なくとも
摺動表面に四三酸化鉄の被膜が形成されているものであ
り、少なくとも摺動表面には、四三酸化鉄の硬質な被膜
と、遊離黒鉛と、多孔部及び遊離黒鉛に含有された潤滑
油とが存在するので、相手材との摺動において摩擦摩耗
特性を大幅に向上させられる。As described above, the cast iron-based sintered sliding member of the present invention has at least the sliding surface of the sintered alloy base material obtained by sintering the chips produced by cutting the grown gray cast iron casting. Is formed with a coating of ferric tetroxide on at least the sliding surface, a hard coating of ferrosoferric oxide, free graphite, and lubricating oil contained in the porous portion and free graphite. Since it exists, the friction and wear characteristics can be greatly improved in sliding with the mating material.
【００７１】また、本発明の鋳鉄系焼結摺動部材の製造
方法では、成長ねずみ鋳鉄鋳物を切削することによって
得られる切粉を焼結して焼結合金母材を形成し、その
後、該焼結合金母材に水蒸気処理を施して焼結合金母材
の表面に四三酸化鉄の被膜を形成するので、摩擦摩耗特
性に優れた鋳鉄系焼結摺動部材を製造できる。Further, in the method for manufacturing a cast iron-based sintered sliding member of the present invention, the chips obtained by cutting the grown gray cast iron casting are sintered to form a sintered alloy base material, and thereafter, Since the sintered alloy base material is subjected to steam treatment to form a coating of ferric tetroxide on the surface of the sintered alloy base material, a cast iron-based sintered sliding member having excellent friction and wear characteristics can be manufactured.
【図１】実施例と比較例の耐荷重試験の結果を比較して
示すグラフである。FIG. 1 is a graph showing a comparison of results of load bearing tests of Examples and Comparative Examples.
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.7 識別記号 ＦＩ テーマコート゛(参考） Ｃ２２Ｃ 37/00 Ｃ２２Ｃ 37/00 Ｅ (72)発明者 小田 裕介 神奈川県藤沢市桐原町８番地 オイレス工 業株式会社藤沢事業場内 Ｆターム(参考） 4K018 AA24 BA13 BB04 BB08 CA02 DA31 FA28 FA42 KA02 ─────────────────────────────────────────────────── ─── Continuation of front page (51) Int.Cl. 7 Identification code FI theme code (reference) C22C 37/00 C22C 37/00 E (72) Inventor Yusuke Oda 8 Kirihara-cho, Fujisawa-shi, Kanagawa OILES Fujisawa Co., Ltd. F-term (reference) 4K018 AA24 BA13 BB04 BB08 CA02 DA31 FA28 FA42 KA02
Claims (10)
って生じる切粉を焼結してなる焼結合金を母材とし、こ
の母材の少なくとも摺動表面に四三酸化鉄の被膜が形成
されていることを特徴とする鋳鉄系焼結摺動部材。1. A sintered alloy obtained by sintering chips produced by cutting a grown gray cast iron casting is used as a base material, and a coating of ferric tetroxide is formed on at least the sliding surface of the base material. A cast iron-based sintered sliding member characterized in that
μｍ以下の範囲内の厚さを有するものであることを特徴
とする請求項１に記載の鋳鉄系焼結摺動部材。2. The coating of ferric tetroxide has a thickness of 2 μm or more and 5 or more.
The cast iron-based sintered sliding member according to claim 1, which has a thickness within a range of μm or less.
さ（ＨｍＶ）が４４０以上５６０以下の範囲内のもので
あることを特徴とする請求項１又は２に記載の鋳鉄系焼
結摺動部材。3. The cast iron-based sintered slide according to claim 1 or 2, wherein the triferric tetroxide coating has a Vickers hardness (HmV) in a range of 440 or more and 560 or less. Moving member.
範囲内の潤滑油が含有されていることを特徴とする請求
項１，２，又は３に記載の鋳鉄系焼結摺動部材。4. The cast iron-based sintered sliding member according to claim 1, wherein the lubricating oil is contained in the range of 7% by volume or more and 15% by volume or less of the total volume. .
し、 この装填した切粉を３トン／ｃｍ２以上５トン／ｃｍ２
以下の範囲内の成形圧力で圧縮成形して圧粉体を形成
し、 中性雰囲気または還元性雰囲気において１１００℃以上
１１５０℃以下の範囲内の温度で３０分間以上９０分間
以下の時間内だけ前記圧粉体を焼結して焼結合金母材を
作製し、 この焼結合金母材に水蒸気処理を施して少なくとも摺動
表面に四三酸化鉄の被膜を形成させることを特徴とする
鋳鉄系焼結摺動部材の製造方法。5. A grown gray cast iron casting is cut, and the chips obtained by this cutting are loaded into a predetermined mold, and the loaded chips are 3 tons / cm 2 to 5 tons / cm 2.
A compact is formed by compression molding at a molding pressure within the following range, and the powder is formed in a neutral atmosphere or a reducing atmosphere at a temperature in the range of 1100 ° C to 1150 ° C for 30 minutes to 90 minutes. A cast iron system characterized by producing a sintered alloy base material by sintering a green compact, and subjecting this sintered alloy base material to steam treatment to form a coating of ferric tetroxide on at least the sliding surface. Manufacturing method of sintered sliding member.
り、ねずみ鋳鉄鋳物のＡ１変態点よりも高い温度とＡ１
変態点よりも低い温度との間で加熱冷却を繰り返す反覆
加熱冷却処理をねずみ鋳鉄鋳物に施すことにより前記成
長ねずみ鋳鉄鋳物を得ることを特徴とする請求項５に記
載の鋳鉄系焼結摺動部材の製造方法。6. In obtaining the grown gray cast iron casting, a temperature higher than the A 1 transformation point and A 1 of the gray cast iron casting are obtained.
The cast iron-based sintered slide according to claim 5, wherein the growing gray cast iron casting is obtained by subjecting the gray cast iron casting to repeated heating and cooling treatments in which heating and cooling are repeated between temperatures lower than the transformation point. A method of manufacturing a member.
たり、 ２０メッシュの篩を通過するが５５メッシュの篩を通過
しない切粉を総重量の８５重量％以上９７重量％以下の
範囲内で前記金型内に装填すると共に、５５メッシュの
篩を通過する切粉を総重量の３重量％以上１５重量％以
下の範囲内で前記金型内に装填することを特徴とする請
求項５又は６に記載の鋳鉄系焼結摺動部材の製造方法。7. A range of 85% by weight or more and 97% by weight or less of the total weight of chips that pass through a 20-mesh screen but do not pass through a 55-mesh screen when the chips are loaded into a predetermined mold. In the inside of the mold, the chips passing through a 55-mesh sieve are loaded in the mold within a range of 3% by weight to 15% by weight of the total weight. 5. The method for manufacturing a cast iron-based sintered sliding member according to 5 or 6.
シュの篩を通過しない切粉を前記金型内に装填するに当
たり、該切粉の総重量のうち、１０重量％以上９０重量
％以下の範囲内であって２０メッシュの篩を通過するが
３６メッシュの篩を通過しない切粉と、１０重量％以上
９０重量％以下の範囲内であって３６メッシュの篩を通
過するが５５メッシュの篩を通過しない切粉とを混合し
て前記金型内に装填することを特徴とする請求項７に記
載の鋳鉄系焼結摺動部材の製造方法。8. When loading chips that pass through a 20-mesh screen but do not pass through a 55-mesh screen into the mold, 10 to 90% by weight of the total weight of the chips is used. Chips that are within the range and pass through the 20-mesh screen but not through the 36-mesh screen, and chips that are within the range of 10 wt% to 90 wt% and pass through the 36-mesh screen but are 55-mesh screen. The method for manufacturing a cast iron-based sintered sliding member according to claim 7, wherein the mixed powder is mixed with chips that do not pass through the mold and loaded into the mold.
以上５５０℃以下の範囲内であって、６０分間以上９０
分間以下の時間内で行うことを特徴とする請求項５から
８までのうちのいずれか一項に記載の鋳鉄系焼結摺動部
材の製造方法。9. The steam treatment has a treatment temperature of 450 ° C.
Within the range of 550 ° C. or higher and 90 minutes or longer of 60 minutes
The method for producing a cast iron-based sintered sliding member according to any one of claims 5 to 8, wherein the method is performed within a time of not more than a minute.
施すに当たり、含油率が該鋳鉄系焼結摺動部材の総体積
の７体積％以上１５体積％以下の範囲内になるように該
鋳鉄系焼結摺動部材に含油処理を施すことを特徴とする
請求項５から９までのうちのいずれか一項に記載の鋳鉄
系焼結摺動部材の製造方法。10. When the cast iron-based sintered sliding member is subjected to oil impregnation treatment, the oil content should be within a range of 7% by volume to 15% by volume of the total volume of the cast iron-based sintered sliding member. The method for producing a cast iron-based sintered sliding member according to any one of claims 5 to 9, wherein the cast iron-based sintered sliding member is subjected to oil impregnation treatment.
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|---|---|---|---|---|
| WO2015098407A1 (en) * | 2013-12-26 | 2015-07-02 | Ntn株式会社 | Machine component using powder compact and method for producing same |
| JP2016053210A (en) * | 2013-12-26 | 2016-04-14 | Ntn株式会社 | Exhaust valve device and gas cushion material |
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2002
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2015098407A1 (en) * | 2013-12-26 | 2015-07-02 | Ntn株式会社 | Machine component using powder compact and method for producing same |
| JP2016053210A (en) * | 2013-12-26 | 2016-04-14 | Ntn株式会社 | Exhaust valve device and gas cushion material |
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