JPS621851A - Manufacture of sliding member - Google Patents
Manufacture of sliding memberInfo
- Publication number
- JPS621851A JPS621851A JP14034385A JP14034385A JPS621851A JP S621851 A JPS621851 A JP S621851A JP 14034385 A JP14034385 A JP 14034385A JP 14034385 A JP14034385 A JP 14034385A JP S621851 A JPS621851 A JP S621851A
- Authority
- JP
- Japan
- Prior art keywords
- crystals
- base material
- layer
- strength
- 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.)
- Pending
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- Coating By Spraying Or Casting (AREA)
Abstract
Description
【発明の詳細な説明】
〔発明の利用分野〕
本発明はＡｌ−Ｓｉ系の過共晶台をコーティングした部
材に係り、％に、基材との密着強度、コーティング層の
強度、耐摩耗性、耐焼付性に優れた摺動部材及びその製
造方法に関する。[Detailed Description of the Invention] [Field of Application of the Invention] The present invention relates to a member coated with an Al-Si based hypereutectic stand, and the present invention relates to a member coated with an Al-Si-based hypereutectic stand, and the adhesive strength with the base material, the strength of the coating layer, and the abrasion resistance are , relates to a sliding member with excellent seizure resistance and a method for manufacturing the same.
ｋｔ−Ｓｉ系合金は耐摩耗材料として比較的古くから用
いられている。この種の合金けＡｌマトリックス中ＶＣ
Ｓ ｉ晶を分散させたもので、Ｓｉ晶の増加に伴って耐
摩耗性は向上する。しかし、Ｓｉ責の増加に伴って強度
、靭性、鋳造性及び塑性加工性等は低下する。したがっ
て、耐摩耗性の良好な過共晶のＡｌ−５ｒ系合金は用途
に大きな制限を受ケているのが現状である。Kt-Si alloys have been used as wear-resistant materials for a relatively long time. VC in this kind of alloyed Al matrix
It is a material in which Si crystals are dispersed, and the wear resistance improves as the Si crystals increase. However, as the Si content increases, strength, toughness, castability, plastic workability, etc. decrease. Therefore, the current situation is that the use of hypereutectic Al-5r alloys with good wear resistance is severely limited.
一般に、耐摩耗材料としては鋳造法によるＡｌ−Ｓｉ系
合金が用いられているが、溶湯からの冷却速度が遅い等
の理由により、共晶及び初晶Ｓｉが大きく、不均一に晶
出している。また、鋳造であるため内部に酸化物の巻込
みあるいは鋳巣等の鋳造欠陥が介在する。したがって、
機械的性質、耐摩耗性が低下し、かつ、これらのばらつ
きも大きい等の欠点がある。また、鋳造材は４０μｍ以
上の角状の初晶Ｓｉ晶が晶出しているため、後述するよ
うな理由により相手材を摩耗させ易い。Generally, Al-Si alloys made by casting are used as wear-resistant materials, but due to reasons such as slow cooling rate from molten metal, eutectic and primary Si crystals are large and non-uniformly crystallized. . Furthermore, since it is cast, there are casting defects such as oxide entrainment or cavities inside. therefore,
It has drawbacks such as decreased mechanical properties and wear resistance, and large variations in these properties. In addition, since the cast material has crystallized angular primary Si crystals of 40 μm or more, it tends to wear out the mating material for reasons described below.
鋳造材の機械的性質を改善する方法として、特開昭５４
−４２３２１号ＶＣは、過共晶ｈｔ−ｓｔ合金鋳造材ｖ
ｃ５０％以上の塑性加工を施こすことが提案されている
。この方法は機械的性質をある程度向上させることには
有効であるが、塑性加工によって角状の粗大初晶Ｓｉの
割れによる靭性の低下がある。As a method for improving the mechanical properties of cast materials,
-42321 VC is a hypereutectic HT-ST alloy casting material v
It has been proposed to perform plastic working with c50% or more. Although this method is effective in improving the mechanical properties to some extent, the toughness decreases due to cracking of the angular coarse primary Si crystals due to plastic working.
一方、急冷凝固させてＳｉ晶を微細する方法として溶射
による方法が知られている。特開昭５６−１１６３８号
及び特開昭５３−６８６１１号では、基材上ＫＡｌ−Ｓ
ｉ系合金を溶射し、初晶Ｓｉを５μｍ以下に微細化せし
めること及び溶射後加熱して固溶Ｓｉを３μｍ以下に析
出させることが提案されている。これらの方法は、Ｓｉ
晶を５μｍ以下にすることにより、相手材の摩耗を減少
させる効果はある。しかし、溶射法＃：を溶射時に溶融
粒子の酸化あるいけ凝固した粒子の巻込み及び空孔等の
欠陥を皆無にすることは極めてむずかしい。On the other hand, a method using thermal spraying is known as a method of rapidly solidifying Si crystals to make them fine. In JP-A-56-11638 and JP-A-53-68611, KAl-S is
It has been proposed to thermally spray an i-based alloy to refine primary Si to 5 μm or less, and to precipitate solid solution Si by heating after thermal spraying to 3 μm or less. These methods
By reducing the crystal size to 5 μm or less, there is an effect of reducing wear of the mating material. However, it is extremely difficult to completely eliminate defects such as oxidation of molten particles, entrainment of solidified particles, and voids during thermal spraying using thermal spraying method #:.
また、溶射の前処理として溶射する基材表面に凹凸の形
成及び表面の活性化を図る目的でプラスチング処理等を
行うが、溶融粒子が基材・＼付着する＠に基材表面が酸
化される場合が多い。したがって、基材と溶射粒子は酸
化膜を介して結合することになり密着性を低下させるこ
とがある。In addition, as a pretreatment for thermal spraying, plasting treatment is performed on the surface of the base material to be thermally sprayed in order to form irregularities and activate the surface. There are many cases where Therefore, the base material and the thermal spray particles are bonded via the oxide film, which may reduce adhesion.
上述したように、溶射法で製造したＡｌ−Ｓｉ系合金は
溶射層の強度及び基材との密着性が十分ではなく、用途
に大きな制限を受けている。As mentioned above, the Al-Si alloy manufactured by thermal spraying has insufficient strength of the thermal sprayed layer and insufficient adhesion to the base material, and its applications are severely limited.
本発明の目的は強度、基材との密着性、耐摩耗性、耐焼
付性に優れた過共晶のＡｌ−Ｓｉ系合金の表面層を有す
る摺動部材及びその製造法を提供することにある。An object of the present invention is to provide a sliding member having a surface layer of a hypereutectic Al-Si alloy having excellent strength, adhesion to a base material, wear resistance, and seizure resistance, and a method for manufacturing the same. be.
本発明げ上記問題点を解決するものであシ、金属材料か
らなる基材上ｖｃＪ共晶のＡｌ−Ｓｉ系合金を溶融状態
から急冷凝固させてコーティング層を形成させることに
よシ微細なＳｉ粒子が均一に分散されたコーティング層
を形成させ、その後熱間塑性加工を施すことによりコー
ティング層の強度、基材との密着性を著しく向上せしめ
たことを特徴とする。The present invention solves the above-mentioned problems by rapidly cooling and solidifying a vcJ eutectic Al-Si alloy from a molten state on a base material made of a metal material to form a coating layer. It is characterized by forming a coating layer in which particles are uniformly dispersed and then subjecting it to hot plastic working, thereby significantly improving the strength and adhesion of the coating layer to the base material.
さらに、本発明は金属基材上に粒径の微細なＳｉ晶が均
一に分散されたコーティング層を形成せしめた後、熱間
塑性加工を施し、その後熱処理を行って粒径３〜２０μ
ｍのＳｉ晶が全ＳＩ晶面積の２０係以上の面積率にする
ことを特徴とする。Furthermore, the present invention involves forming a coating layer in which Si crystals having a fine grain size are uniformly dispersed on a metal base material, and then subjecting the layer to hot plastic working, followed by heat treatment to form a coating layer with a grain size of 3 to 20 μm.
It is characterized in that the area ratio of m Si crystals is 20 times or more of the total SI crystal area.
第１図は、本発明の摺動部材の製造工程と従来法の製造
工程を示す。本発明と従来法の大きな相違点はｈｔ−ｓ
ｒ系合金を急冷凝固し念後、熱間塑性加工を施すことに
ある。FIG. 1 shows the manufacturing process of a sliding member according to the present invention and the manufacturing process of a conventional method. The major difference between the present invention and the conventional method is that h-s
The purpose is to rapidly solidify the r-based alloy and then subject it to hot plastic working.
すなわち、本発明の摺動部材はコーティングによってＳ
ｉ晶を微細化せしめた層を形成した後、熱間塑性加工を
行って層内にある空孔をおしつぶし、基材とコーティン
グ層間の酸化膜を分断することによって、一体化あるい
は密着性を良好にし、Ｓｉ晶の割れがなく、コーティン
グ層の強度及び基材との密着性を著しく向上せしめたも
のである。That is, the sliding member of the present invention has S
After forming a layer with finer i-crystals, hot plastic processing is performed to crush the pores in the layer and divide the oxide film between the base material and the coating layer to improve integration or adhesion. The coating layer has good properties, no cracking of the Si crystal, and significantly improved strength of the coating layer and adhesion to the base material.
さらにもう１つの発明は、上記発明のコーティング及び
熱間塑性加工を行った後、熱処理を行ってＳｉ晶の粒径
を全Ｓｉ晶面積の２０係以上が３〜２０μｍになるよう
にすることによって、耐摩耗性を向上させたものである
。Yet another invention is that after the coating and hot plastic working of the above invention, heat treatment is performed so that the grain size of the Si crystals is such that the 20th factor or more of the total Si crystal area is 3 to 20 μm. , with improved wear resistance.
Ａｌ−Ｓｉ系合金は含有するＳｉ量によって亜共晶、共
晶及び過共晶に大別される。亜共晶合金は過共晶合金に
比べて耐摩耗性か劣るため、通常、摺動部材としては共
晶組成以上のＳｉを含有するＡｌ−Ｓｉ系合金が主に用
いられている。この種の合金は軟質なＡｌマトリックス
中［Ｈｖ１０００程度の硬い３ｉ晶を分散させて耐摩耗
性を向上させている。したがって、マトリックス中に分
散しているＳｉの滑、大きさ、分散状態及びマトリック
スの強度等により耐摩耗性は著しく異なる。すなわち、
ｈｔ−ｓｉ系合金の摺動部材として汀、Ｓｉ晶の量が多
く、ある程度の大きさをもつＳｉ晶を均一に分散させた
強度の強いものが望ましい。Al-Si alloys are roughly classified into hypoeutectic, eutectic, and hypereutectic depending on the amount of Si contained. Since hypoeutectic alloys have inferior wear resistance compared to hypereutectic alloys, Al-Si alloys containing Si in a eutectic composition or higher are usually used as sliding members. This type of alloy improves wear resistance by dispersing hard 3i crystals of about 1000 Hv in a soft Al matrix. Therefore, the wear resistance varies significantly depending on the slippage, size, dispersion state of Si dispersed in the matrix, strength of the matrix, etc. That is,
As a sliding member of the ht-si alloy, it is desirable to use a material with high strength and a large amount of Si crystals, in which Si crystals of a certain size are uniformly dispersed.
ｈｔ−ｓｉ系合金の摺動部材としては、主に鋳造によっ
て製造されているが、一部溶射によっても作製されてい
る。鋳造によって製造したものは前述したように、初晶
Ｓｉが角状、粗大に晶出し、５ｉｌｌも強度とのかねあ
いから２０俤前後が通常使用される限度である。また、
鋳造材は内部に鋳巣あるいは酸化物の巻き込み等の欠陥
が介在するため、信頼性が低い。％Ｖｃ、 Ａｌ合金は
切欠感受性が高いために、表面あるいけ表面近傍の欠陥
は繰返し応力の加わるような使用状態ではこれらを起点
として割れが発生し易い。これらの欠点の改善策として
は、塑性加工を行って空孔等を押しつぶすことが考えら
れる。しかし、過共晶のＡｌ−８ｔ系合金は塑性加工性
が悪いため、強加工を行うことは非常にむずかしい。好
条件下で塑性加工ができたとしても初晶Ｓｉが割れる問
題が生ずる。すなわち、過共晶のＡｌ−５：系合金の鋳
造材は冷却速度が遅いため、角状の粗大な初晶Ｓｉが晶
出している。この初晶Ｓｉは硬くて戦い性質を有し、か
つ、角状で粗大なためにマトリックスの変形に伴って移
動しニ〈く、割れが発生する。このような３ｉ晶の割れ
のあるものを摺動部材に用いた場合は、Ｓｉ晶が脱落し
易いために、仕上げ加工時あるいけ使用時Ｔｉｃ Ｓ
ｉ晶が脱落して耐摩耗性が低下する。特に、使用時に脱
落し九場合は、脱落したＳｌが摩擦面に介入し、摩擦面
に傷をつけたりあるいけ研摩剤となって摩耗を促進する
。Sliding members made of ht-si alloys are mainly manufactured by casting, but some are also manufactured by thermal spraying. As mentioned above, in the case of products manufactured by casting, the primary Si crystallizes in a angular and coarse shape, and 5ill is the limit that is usually used due to the conflict with strength. Also,
Cast materials have low reliability because they have internal defects such as cavities or oxide entrainment. %Vc, Since Al alloys are highly sensitive to notches, defects on or near the surface are likely to cause cracks as starting points under conditions of use where repeated stress is applied. As a measure to improve these shortcomings, it is possible to perform plastic working to crush the pores and the like. However, hypereutectic Al-8t alloy has poor plastic workability, so it is very difficult to perform strong working. Even if plastic working is possible under favorable conditions, the problem arises that primary Si crystals crack. That is, since the cooling rate of the cast material of the hypereutectic Al-5: alloy is slow, coarse angular primary Si crystals are crystallized. This primary Si crystal is hard and has fighting properties, and since it is angular and coarse, it does not move with the deformation of the matrix, causing cracks. When such cracked 3i crystals are used for sliding parts, the Si crystals tend to fall off, so Tic S crystals are not used during finishing or during use.
i-crystals fall off and wear resistance decreases. Particularly, if it falls off during use, the fallen Sl intervenes on the friction surface, damages the friction surface, or acts as an abrasive, accelerating wear.
一方、摺＃Ｊ＠材の摩擦面表面に過共晶のＡｌ−Ｓｉ系
合金を溶射したものは、溶射層中のＳｉ晶が微細、かつ
均一に分散した状態となるが、溶射層内には空孔、表面
酸化粒子あるい汀付着する前に凝固した粒子等が存在す
る。したがって、溶射層の強度が低く、空孔等が起点と
なって割れの発生原因となる。また、基材と溶射層の密
着強度は、通常、２〜３ ”／Ｍ”程度であり、密着強
度が低いことが実用上の大きな障害になっている。溶射
を行う場合は、通常、基材表面にプラスチング処理を行
って、表面に凹凸を形成すること及び表面の酸化膜を除
去して活性化させる。しかし、基材表面はプラスチング
後あるいは溶射中ＶＣある程度酸化膜が形成される。し
たがって、基材と溶射層は酸化膜を介して結合する部分
が多く、密着強度は極めて低い。On the other hand, when a hypereutectic Al-Si alloy is thermally sprayed onto the friction surface of Suri #J@ material, the Si crystals in the thermally sprayed layer are finely and uniformly dispersed; There are pores, surface oxidized particles, and particles that solidified before being deposited on the surface. Therefore, the strength of the sprayed layer is low, and pores and the like become starting points and cause cracks to occur. Further, the adhesion strength between the base material and the sprayed layer is usually about 2 to 3 ''/M'', and the low adhesion strength is a major obstacle in practical use. When performing thermal spraying, the surface of the base material is usually subjected to a plasting treatment to form irregularities on the surface and to remove and activate the oxide film on the surface. However, a certain amount of VC oxide film is formed on the surface of the base material after plasting or during thermal spraying. Therefore, the base material and the sprayed layer are often bonded via oxide films, and the adhesion strength is extremely low.
ところで、摺動部材の摩耗現像であるが、２つの固体を
すべらせると摩擦を生ずる。この固体間に液体や固体な
どの潤滑剤を挿入すると摩擦力は著しく低下する。しか
し、高負荷あるいは高速摺動時Ｖｃは、固体間に挿入さ
れた潤滑剤は一部分あるいは全面に介在しなくなり、固
体同志の接触が生じて摩擦力は増大して、異状摩耗や焼
付き等が発生する。これらを防止するためには、潤滑剤
を接触面に常に介在きせる必要があり、摺動部材自身に
潤滑剤の保持作用あるいけ摩擦係数が小きく、潤滑作用
の優れた物質を含有しているものが望ましい。By the way, as for the wear and tear of sliding members, when two solid objects slide, friction occurs. When a liquid or solid lubricant is inserted between these solids, the frictional force is significantly reduced. However, during high-load or high-speed sliding Vc, the lubricant inserted between the solids disappears partially or completely, and the solids come into contact with each other, increasing the frictional force and causing abnormal wear, seizure, etc. Occur. In order to prevent these, it is necessary to always have a lubricant present on the contact surfaces, and the sliding member itself contains a substance that has a low friction coefficient and has an excellent lubricating effect, so that it can retain the lubricant. Something is desirable.
Ａｌ−Ｓｉ系合金ＨＡｌマトリックス中１ｃＳｉ晶が分
散した状態を呈し、軟質なマトリックスは硬質な８１晶
よりも摩耗が大きいために、マトリックスげ凹部となシ
、潤滑剤の保持作用を受けもつ。The 1cSi crystals are dispersed in the Al-Si based alloy HAl matrix, and since the soft matrix is more abrasive than the hard 81 crystals, the matrix retains the lubricant by forming recesses.
すなわち、硬いＳｉ晶で荷重を支え、軟質なマトリック
スに形成される凹部が潤滑剤を保持するために耐摩耗性
が良好になる。した力１つて、マトリックス中に分散し
ているＳｉ晶の量、分散状態、大きさによって耐摩耗性
、耐焼付性は著しく異なる。すなわち、Ｓｉ量が少ない
とＳｉに加わる荷重が大きくなり、分散が不均一な場合
あるいは含有するＳｉ量は同じでもＳｉ晶が粗大な場合
は局部的に応力がかかるため、焼付きあるいけ異状摩耗
の発生原因となる。また、角状の粗大Ｓｉ晶が不均一に
分散した状態では、摩擦によってマトリックスが早く摩
耗し、角状の粗大Ｓｉ晶が突出して相手材に傷をつけ、
傷が生ずると摩耗は促進される。一方、Ｓｉ晶が微細過
ぎた場合は、マトリックスの摩耗が進むにつれてＳｉ晶
が脱落し易く、Ｓｉ量が減少するとともに脱落しｆｔ：
、 Ｓ ｉ晶が摩擦面に介入して耐摩耗性が低下する。That is, the hard Si crystal supports the load, and the recesses formed in the soft matrix retain the lubricant, resulting in good wear resistance. However, the wear resistance and seizure resistance vary significantly depending on the amount, state of dispersion, and size of Si crystals dispersed in the matrix. In other words, if the amount of Si is small, the load applied to the Si will be large, and if the dispersion is uneven, or if the amount of Si contained is the same but the Si crystals are coarse, stress will be applied locally, resulting in seizure or abnormal wear. This causes the occurrence of In addition, when the angular coarse Si crystals are unevenly dispersed, the matrix wears out quickly due to friction, and the angular coarse Si crystals protrude and damage the mating material.
Wear is accelerated when scratches occur. On the other hand, if the Si crystals are too fine, they tend to fall off as the matrix wears out, and as the amount of Si decreases, they fall off.ft:
, Si crystals intervene on the friction surface and wear resistance decreases.
本発明は上述し之ような問題点及び摩耗現象を鑑みてな
され念ものである。The present invention has been devised in view of the above-mentioned problems and wear phenomena.
本願発明者らは種々検討し念結果、溶融状態から冷却速
度を速くし、基材上にコーティングして、急凝させて過
共晶のｈｔ−ｓ：系合金を金属基材上にコーティングし
、Ａｌ中へのＳ】の過飽和同浴状態あるいはＳｉ晶とし
て微細、かつ、均一に分散せしめた後、熱間塑性加工を
施すことによって、Ｓｉ晶の割れがなく、コーティング
層の強度及び基材との密着性が著しく高くなることを見
いだした。さらに、コーティング及び熱間塑性加工を行
った後、加熱処理を施して３ｉ粒径を調整することによ
って、相手材の摩耗を減少させること及び耐摩耗性、耐
焼付性が良好にさせることができることを明にした。The inventors of the present application conducted various studies and found that the cooling rate from the molten state was increased, the coating was applied onto the base material, and the hypereutectic HT-S alloy was coated onto the metal base material. , S] is finely and uniformly dispersed in a supersaturated bath state or as Si crystals in Al, and then subjected to hot plastic processing, there is no cracking of the Si crystals, and the strength of the coating layer and the base material are improved. It was found that the adhesion with Furthermore, by applying heat treatment after coating and hot plastic working to adjust the 3i grain size, wear of the mating material can be reduced and wear resistance and seizure resistance can be improved. revealed.
以下、本発明の詳細な説明する。The present invention will be explained in detail below.
本発明の摺動部材の基材は鉄系金属あるいは非鉄金属の
いずれも用いることができる。The base material of the sliding member of the present invention can be either a ferrous metal or a non-ferrous metal.
本発明の摺動部材の表面に形成するｈｔ−ｓｉ系合金コ
ーティング層のＳｉｉは、を量係で１５〜５０チが好ま
しい。共晶組成以下では所望の耐摩耗性が得られず、５
０重ｌｌ−係を越えると靭性が低下して熱間塑性加工性
が悪くなり、割れあるいは剥離の生ずるおそれがある。The Sii of the HT-Si alloy coating layer formed on the surface of the sliding member of the present invention is preferably 15 to 50 in terms of quantity. If the composition is lower than the eutectic composition, the desired wear resistance cannot be obtained;
If it exceeds 0 weight/ll-modulus, the toughness decreases, the hot plastic workability deteriorates, and there is a risk of cracking or peeling.
望ましくは２０〜４０重量係が良い。Desirably, the weight ratio is 20 to 40.
コーティング層の厚さは任意でよいが０１簡以上が望ま
しい。すなわち熱関塑曲加工によってコーティング層の
厚ａｈさらに薄くなること及び仕上げ加工時に基材が露
出するおそれがある。The thickness of the coating layer may be arbitrary, but preferably 0.01 mm or more. That is, there is a risk that the thickness of the coating layer ah may become even thinner due to thermal bending and that the base material may be exposed during finishing processing.
コーティング層の強度及び耐食性を高めるために添加す
る場合のＣｕ及びＭｇ量は、Ｃｕ０．５〜５ｇＬ量チ、
Ｍｇ０．０５〜５重を俤が好ましい。The amount of Cu and Mg added to improve the strength and corrosion resistance of the coating layer is 0.5 to 5 gL of Cu,
It is preferable to use 0.05 to 5 times Mg.
ＣｕｔｆＡｌとＣｕｔＡｌを形成して強度を高めるが０
．５チ未満ではその効果が少ない。Ｃｕの添加効果は０
．５チ以上で効果が大になり、７チでほぼ飽和する。し
たがって、０．５〜５重ｆｆｉ％とした。CutfAl and CutAl are formed to increase the strength, but 0
．． If the number is less than 5 inches, the effect will be small. The effect of adding Cu is 0
．． The effect becomes large at 5 inches or more, and is almost saturated at 7 inches. Therefore, it was set to 0.5 to 5 times ffi%.
望ましくけ２〜３重量％である。また、ＭｇはＳｉとＭ
ｇ、Ｓｉを形成して強度及び耐食性を高めるが、０．０
５％未満の添加でにほとんど効果がない。It is preferably 2 to 3% by weight. Also, Mg is Si and M
g, forms Si to increase strength and corrosion resistance, but 0.0
Addition of less than 5% has almost no effect.
０、０５１以上になると機械的性質が増加しけじめ、０
．５俤を越えると耐食性も顕著に改善される。機械的性
質とシわけ引張強ざの増大ｉ １．５ ％でほぼ飽和状
態に達し、耐食性も５チで一定となる。したがって、Ｍ
ｇ′！には０．０５〜５チとする。望ましくけ０．２〜
２重量憾が良い。When the value exceeds 0.051, the mechanical properties increase and become 0.
．． When it exceeds 5 yen, corrosion resistance is also significantly improved. The increase in mechanical properties and wrinkle tensile strength reaches a nearly saturated state at 1.5%, and the corrosion resistance also becomes constant at 5 cm. Therefore, M
g'! 0.05 to 5 inches. Desirable value: 0.2~
2 weight is good.
さらに、ｐｂ、 ｐｂ金合金Ｓｎ、Ｓｎ合金等の低融点
金属を１〜５重量％、あるいはグラファイト、Ｍｏ５ｔ
＋ ＢＮ等の固体潤滑剤を１〜３重量係含有きせると耐
焼付性、耐摩耗性はざらに向上する。Furthermore, 1 to 5% by weight of a low melting point metal such as pb, pb gold alloy Sn, Sn alloy, or graphite, Mo5t.
+ When a solid lubricant such as BN is contained in a weight ratio of 1 to 3, the seizure resistance and wear resistance are greatly improved.
低融点金属あるいは固体潤滑剤の含有量が１チ未満でけ
その効果が少なく、低融点金属が５チあるいは固体潤滑
剤が３重量係を越えると、熱間塑性加工性が低下して割
れが生ずるおそれがある。したがって、低融点金属げ１
〜５重量％、固体潤滑剤は１〜３重量％とした。If the content of the low melting point metal or solid lubricant is less than 1 inch, the scraping effect will be small, and if the content of the low melting point metal or solid lubricant exceeds 5 inch, or the solid lubricant content exceeds 3 weight coefficient, the hot plastic workability will decrease and cracking will occur. There is a risk that this may occur. Therefore, low melting point metal 1
~5% by weight, and solid lubricant from 1 to 3% by weight.
次に、本発明の摺動部材の製造方法について説明する。Next, a method for manufacturing a sliding member according to the present invention will be explained.
本発明の摺動部材を製造する念めのコーティング法は溶
融状態からの凝固時の冷却速度が少なくとも１００Ｃ／
（３）以上にする方法であればいずれの方式でもよい。The preliminary coating method for manufacturing the sliding member of the present invention has a cooling rate of at least 100C/
(3) Any of the above methods may be used.
例えば固体を再溶融する方式としては溶射方法があり、
プラズマ溶射、アーク溶射、ガス浴射、爆発溶射の方法
があるが、高エネルギーによシ短時間で溶融し、溶融粒
子が加速されて付着するため付着強度が強く、かつ、使
用ガスがＡｒ、 Ｈｅ、 Ｈｌ 、 Ｎ２等であるため
に溶融粒子の酸化の少ないプラズマ溶射法が望ましい。For example, thermal spraying is a method for remelting solids.
There are methods such as plasma spraying, arc spraying, gas bath spraying, and explosive spraying, but they use high energy to melt in a short time, the molten particles are accelerated and adhere, so the adhesion strength is strong, and the gas used is Ar, Plasma spraying is desirable because it uses He, Hl, N2, etc., and therefore causes less oxidation of the molten particles.
コーティングを行う場合の雰囲気は大気中でもきしつか
えないが、Ａｌ系合金は酸化膜の形成速度が早いため、
酸化を防止する上からＡｒガス雰囲気中でコーティング
することが望ましい。また、ｈｔ−ｓｒ系材１ｃＭｇ、
ｐｂあるいｈｓｎ等の平衡蒸気圧の高い成分が含有して
いる場合は、大気中でコーティングすると作業中にこれ
らの成分が蒸発して成分の安定したコーティング層が得
られにくい。これらの防止対策としては減圧雰囲気中コ
ーティングすると、よシ成分の安定した層が得うレる。Although the atmosphere for coating is not harsh even in the air, Al-based alloys form an oxide film quickly, so
It is desirable to coat in an Ar gas atmosphere to prevent oxidation. In addition, ht-sr material 1 cMg,
If components with high equilibrium vapor pressure such as pb or hsn are contained, if coating is performed in the atmosphere, these components will evaporate during the operation, making it difficult to obtain a coating layer with stable components. To prevent these problems, coating in a reduced pressure atmosphere will provide a stable layer of good components.
さらに、平行蒸気圧の高い成分のもの及びグラファイト
等の比重の小ざいものけ、粉末粒子に金属めっき等を施
してコーティングすると成分の安定した層が形成される
。したがって、固体潤滑剤及び平衡蒸気圧の高い成分を
含有するＡｌ−Ｓｉ系合金をコーティング下る場合は、
減圧下でＡｒガスを導入しながらコーティングすること
がよシ望ましい。Furthermore, a stable layer of the components can be formed by applying metal plating or the like to coating powder particles of components with high parallel vapor pressure and small specific gravity such as graphite. Therefore, when coating an Al-Si alloy containing a solid lubricant and components with high equilibrium vapor pressure,
It is more desirable to perform coating while introducing Ar gas under reduced pressure.
次に、上述したような方法によりｋｌ−Ｓｉ系合金をコ
ーティングした部材をコーティング層の再結晶温度以上
〜融点以下の温度でコーティング層の断面減少率で１０
％以上の塑性加工を施す。塑性加工温度が再結晶温度以
下では、強加工すると割れあるいは基材との剥離が生ず
るおそれがあり、融点以上ではコーティング層が流出す
る。加工率及び含有成分によっても多少異なるが、望ま
しくけ３００〜５５０Ｃ程度が良い。加工率であるが１
０％未満では空孔等の押しつぶしあるいけ酸化膜の分断
が不十分で、コーティング層の強度及び基材との密着強
度の向上があまシ期待できない。Next, the member coated with the kl-Si alloy by the method described above is heated at a temperature between the recrystallization temperature and the melting point of the coating layer to reduce the area reduction rate of the coating layer to 10.
% or more of plastic working. If the plastic working temperature is below the recrystallization temperature, severe working may cause cracking or separation from the base material, and if the plastic working temperature is above the melting point, the coating layer will flow out. Although it varies somewhat depending on the processing rate and the components contained, it is preferably about 300 to 550C. The processing rate is 1
If it is less than 0%, the crushing of pores and the like and division of the oxide film will be insufficient, and no improvement in the strength of the coating layer and the adhesion strength to the substrate can be expected.
したがってコーティング層の加工率＃’！１０１以上と
し念。望ましくは２０チないしそれ以上が良い。Therefore, the processing rate of the coating layer is #'! I hope it's over 101. Preferably it is 20 inches or more.
これらの塑性加工を施すことによって、強度が強く、基
材との密着性の優れた部材が得られる。さらに、必要に
より塑性加工後に溶体化処理をし、時効処理をすること
によって目的とする摺動部材が得られる。By performing these plastic workings, a member with high strength and excellent adhesion to the base material can be obtained. Further, if necessary, after plastic working, solution treatment and aging treatment are performed to obtain the intended sliding member.
本発明のもう一つの製造方法は、上述したコーティング
及び熱間塑性加工を行った後、ざらに加熱処理を行って
３〜２０μｍのＳｉ晶を全Ｓｉ晶面積の２０％以上粒径
に調整する。３μｍ未溝Ｏｓｉ粒径が大半を占める摺動
部材では、前述したように、マトリックスの摩耗に伴っ
てＳｉ晶の脱落が激しくなって耐摩耗性が低下すること
がある。Another manufacturing method of the present invention is to perform the above-mentioned coating and hot plastic working, and then perform rough heat treatment to adjust the particle size of Si crystals of 3 to 20 μm to 20% or more of the total Si crystal area. . In a sliding member in which the majority of ungrooved Osi grains have a diameter of 3 μm, as described above, as the matrix wears, the Si crystals may fall off more frequently and the wear resistance may deteriorate.
２０μｍ以上のＳｉ晶が大半を占める場合は、Ｓｉ晶の
脱落による摩耗は少なくなるが、層の靭性が低くなる。When Si crystals with a diameter of 20 μm or more occupy the majority, wear due to shedding of Si crystals is reduced, but the toughness of the layer is reduced.
したがって、ｈｔ−ｓｉ系合金の耐摩耗性も減少するこ
となく、靭性の高いＳｉ晶粒径は３〜２０μｍ程度がよ
く、これらの割合が２０−以下であると、ｈｔ−ｓｔ系
合金の耐摩耗性が小さくなる。加熱処理によってＳｉ粒
径を調整を行った後、必要に応じて、通常行なわれてい
る溶体化処理をし、時効処理することによって目的とす
る摺動部材を作製することができる。Therefore, the wear resistance of the HT-Si alloy does not decrease, and the Si crystal grain size with high toughness is preferably about 3 to 20 μm, and if the ratio of these is 20 or less, the wear resistance of the HT-ST alloy increases. Less abrasive. After the Si particle size is adjusted by heat treatment, the desired sliding member can be manufactured by subjecting it to a commonly used solution treatment and aging treatment, if necessary.
上述したような方法によシ作製した摺動部材は、ｋｌ−
Ｓｉ系合金の強度、基材との密着性、耐摩耗性及び相手
材の摩耗を少なくする優れた摺動部材が得られる。The sliding member manufactured by the method described above has a kl-
A sliding member with excellent Si-based alloy strength, adhesion to the base material, wear resistance, and reduced wear of the mating material can be obtained.
以下、本発明の詳細な説明する。 The present invention will be explained in detail below.
実施例１
基材として８８４１（３０Ｘ７０Ｘ５ｔ）及びＡｌ材２
０１７を用い、溶射すべき面に５ ｋｇ ／ ｃｗｔ”
の圧力によりプラスチング処理を行った。この基材に第
１表に示した組成のアトマイズ法で作製した粒径１０〜
４４μｍのｋｌ−Ｓｉ系合金をプラズマ溶射法により溶
射した。コーティングは、減圧中でＡｒガスを導入しつ
つ、プラズマガス組成Ａｒ／Ｈ２＝１００ニア、電流８
００Ａ、溶射距離１００聰の溶射条件でコーティングし
た。なお、第１表の合金のその他の成分は不可避不純物
を除きｋｔである。Example 1 8841 (30X70X5t) and Al material 2 as base material
017 and 5 kg/cwt” onto the surface to be sprayed.
Plasting treatment was performed using the pressure of On this base material, particles with a particle size of 10~
A 44 μm thick kl-Si alloy was sprayed by plasma spraying. Coating was performed under reduced pressure while introducing Ar gas, plasma gas composition Ar/H2 = 100 near, current 8.
Coating was carried out under thermal spraying conditions of 00A and a spraying distance of 100 meters. Note that the other components of the alloys in Table 1 are kt except for inevitable impurities.
これら溶射した試料を４６００で３０分加熱して圧延に
よシ塑性加工を行った。圧延は１パスの厚ざ減少率を３
チとし、最高６０係まで行った。これらの試料を、ざら
［５ｏｏｔ：’で１時間加熱して水冷し、その後１７０
Ｃで８時間の時効処理を行って試験片に用いた。比較材
として、従来材である溶射のまま及び鋳造法で作製した
ものであり、鋳造材は本発明と同様の塑性加工を行った
。また、これら比較材についても、５００Ｃで１時間加
熱して水冷し、その後１７０Ｃで８時間の時効処理を行
った。These sprayed samples were heated at 4600° C. for 30 minutes and plastically worked by rolling. For rolling, the thickness reduction rate per pass is 3
I reached a maximum of 60. These samples were heated in a colander [5oot:' for 1 hour, cooled in water, and then heated to 170
It was aged for 8 hours at C and used as a test piece. Comparative materials were prepared by thermal spraying, which is a conventional material, and by a casting method, and the cast materials were subjected to plastic working in the same manner as in the present invention. These comparative materials were also heated at 500C for 1 hour, cooled with water, and then aged at 170C for 8 hours.
第２図は代表的な断面顕微鏡組織写真を示す。FIG. 2 shows a typical cross-sectional microscopic microstructure photograph.
第２図（Ａ）ｔ−を本発明材の試料番号５のもので、溶
射後、厚で減少率で４０％の熱間圧延を行ったものであ
る。第２図（Ｂ）け比較材１の溶射のまま、第２図（Ｃ
）は比較材２の鋳造材に４０チの熱間圧延を施したもの
である。図からも明らかなように、本発明材は３〜５μ
ｍ以下の微細なＳｉ晶が均一に分散しており、空孔もな
く、Ｓｉ晶の割れも認められず健全である。これに比し
、比較材１の溶射のままは、３〜５μｍ以下のＳｉ晶が
均一に分散しているが、空孔が認められ、比較材２の鋳
造材を圧延したものは、８１晶が粗大であり、塑性加工
による粗大Ｓｉ晶の割れが認められる。したがって、本
発明材は比較材１及び２よりも健全な組織を呈している
ことがわかる。FIG. 2(A) t- is sample number 5 of the material of the present invention, which was hot-rolled at a thickness reduction rate of 40% after thermal spraying. Figure 2 (B) Comparative material 1 as sprayed, Figure 2 (C)
) is a cast material of comparative material 2 subjected to 40 inch hot rolling. As is clear from the figure, the material of the present invention is 3 to 5μ
Fine Si crystals of m or less in size are uniformly dispersed, there are no vacancies, and no cracks in the Si crystals are observed, making it sound. In contrast, in the as-sprayed comparative material 1, Si crystals of 3 to 5 μm or less are uniformly dispersed, but pores are observed, and in the rolled cast material of comparative material 2, 81 crystals are dispersed. is coarse, and cracks in the coarse Si crystals due to plastic working are observed. Therefore, it can be seen that the material of the present invention has a healthier structure than Comparative Materials 1 and 2.
第２表はＡｌ＝Ｓｉ系合金と基材の密着強度及びｈｔ−
ｓｉ系合金層の引張試験結果を示す。本発明材は、従来
材である比較材１の溶射のまま及び比較材２の鋳造材に
熱間圧延を施したものよりも、基材との密着強は、引張
強ざ及び伸びが優れていることがわかる。したがって、
本発明材は強度、靭性が著しく高く、従来の問題を解消
し、実用範囲を大巾に改善できる。Table 2 shows the adhesion strength and ht-
The tensile test results of the Si-based alloy layer are shown. The material of the present invention has superior adhesion strength to the base material, tensile strength and elongation, compared to the conventional material Comparative Material 1 as-sprayed and Comparative Material 2 which is a hot-rolled cast material. I know that there is. therefore,
The material of the present invention has extremely high strength and toughness, solves the conventional problems, and can greatly improve the practical range.
実施例２
Ｓ４５Ｃ（５０Ｘ７０Ｘ１０ｔ）を基材として、実施例
１と同様の条件で第１表の賦香３．５．７．９の成分を
溶射、塑性加工を行った後、５３０Ｃ以上の温度で加熱
して、３〜２０μｍのＳｉが全３ｉ晶面積に占める割合
を調整した。これらを回転式摩耗試験機（ビン−ディス
ク型）のビン側試験片として摩耗試験を行った。試験条
件は、相手材：５４５Ｃ（Ｈｖ ： ２００ ）、荷重
： ｌ ２０ｋｇ／ｍ”、摩擦速度ニアｍ／ｓ、潤滑油
：タービン油＄１４０、試験時間：５時間でろる。なお
、比較材として、実施例１と同様の試験片を用いた。Example 2 Using S45C (50 x 70 x 10 t) as a base material, the ingredients listed in Table 1 for flavoring 3.5.7.9 were thermally sprayed and plastically worked under the same conditions as in Example 1, and then at a temperature of 530 C or higher. The ratio of 3 to 20 μm of Si to the total 3i crystal area was adjusted by heating. Abrasion tests were conducted using these as specimens on the bottle side of a rotary abrasion tester (bin-disk type). The test conditions were: mating material: 545C (Hv: 200), load: l 20kg/m'', friction speed near m/s, lubricating oil: turbine oil $140, test time: 5 hours. , the same test piece as in Example 1 was used.
第３図は本発明材の賦香８の加熱処理後の断面顕微鋼組
織を示、す。図を見ても明らかなように、加熱処理によ
ってＳｉ＆ｔｌ’１大きくなシ、１０μｍ前後のＳｉ晶
が分散しているのがわかる。FIG. 3 shows a cross-sectional microscopic steel structure of the inventive material 8 after heat treatment. As is clear from the figure, it can be seen that Si&tl'1 large Si crystals, approximately 10 μm in size, are dispersed by the heat treatment.
第４図ｔｆ′１Ａｌ−３２係Ｓｉ系合金溶射層内の３〜
２０μｍのＳｉ晶が全Ｓｉ晶面積に占める割合と摩耗量
の関係を示す。３〜２０μｍの全３ｉ晶面積が２０俤程
度になると摩耗量げ低下し、その後ゆるやかに小さくな
る。したがって、２０チ以上が好ましい。Fig. 4 tf'1 Al-32 Si-based alloy sprayed layer 3~
The relationship between the ratio of 20 μm Si crystal to the total Si crystal area and the amount of wear is shown. When the total 3i crystal area of 3 to 20 μm reaches about 20 squares, the amount of wear decreases, and then gradually decreases. Therefore, 20 inches or more is preferable.
第５図は本発明材と比較材の摩耗試験結果を示す。本発
明材の賦香５け同−Ｓｉ量である比較材１の溶射のまま
及び比較材２の鋳造材に塑性加工を施したものに比し、
摩耗量が小ざく、耐摩耗性が良好であることがわかる。FIG. 5 shows the abrasion test results for the present invention material and comparative material. Compared to the as-sprayed Comparative Material 1, which has the same Si content as the inventive material, and the Comparative Material 2, which is a cast material that has undergone plastic working.
It can be seen that the amount of wear is small and the wear resistance is good.
実施例３
基材としてＡｌ材（２０２４）５０Ｘ７０Ｘ１０ｔを用
い、ｈｔ−ｓ；系合金（Ａｌ ２５８ ｉ −３Ｃｕ
Ｏ，５Ｍｇ） のアトマイズ粉（１０〜４４μｍ）と
固体潤滑剤との混合粉を実施例１と同様の溶射条件で溶
射した。但し、固体潤滑剤のｐｂ、グラファイトｒｌ
Ｃｕメッキを施したものを使用した。これらの固体潤滑
剤の添加割合を第３表に示す。溶射した試料を４５００
で３０分加熱して圧延機によシ、加工率４０％の塑性加
工を行つ念。これらを実施例２と同様の回転式摩耗試験
機によυ、耐焼付性試験を行った。試験条件は、相手材
： Ｆ’ＣＤ４５高周波焼入れ材（ＨＲＣ６０）、摩擦
速度： ｌ Ｏｍ／ｓ、潤滑油：冷凍機用オイル、試験
時間：各面圧下で１５分間、荷重＋１０ｋｇ／口２間隔
で試験した。なお、比較材は実施例１と同様であり、溶
射のまま及び鋳造を熱間圧延したものである。Example 3 Al material (2024) 50X70X10t was used as the base material, ht-s; type alloy (Al 258 i -3Cu
A mixed powder of an atomized powder (10 to 44 μm) of O, 5Mg) and a solid lubricant was sprayed under the same spraying conditions as in Example 1. However, solid lubricants PB, graphite RL
The one plated with Cu was used. Table 3 shows the addition ratios of these solid lubricants. The sprayed sample was 4500
Heat it for 30 minutes and put it in a rolling machine to perform plastic working at a processing rate of 40%. These were subjected to a seizure resistance test using the same rotary abrasion tester as in Example 2. The test conditions were: mating material: F'CD45 induction hardened material (HRC60), friction speed: 1 Om/s, lubricating oil: refrigerator oil, test time: 15 minutes under each surface pressure, load + 10 kg/mouth 2 intervals. Tested. The comparative materials are the same as those of Example 1, and are thermally sprayed as-is or cast and hot-rolled.
＠６図げ耐焼付性試験結果を示す。図から明らかなよう
に、本発明の固体潤滑剤が含有されているものは、比較
材１及び−２ＶＣ比較して耐焼付荷重が犬きく、耐焼付
性に優れていることがわかる。@6 Shows the results of the seizing resistance test. As is clear from the figure, the product containing the solid lubricant of the present invention has a higher seizure resistance compared to Comparative Materials 1 and -2VC, indicating that it has excellent seizure resistance.
以上の結果より明らかなように、本発明の摺動部材は、
基材との密着性、コーティング層の強度、耐摩耗性、耐
焼付性に優れ、従来の鋳造あるいは溶射のままのもので
問題のあった点を改善した優れた摺動部材である。特に
、基材との密着強度及びコーティング層の強度の改善に
より、広範囲利用できる。また、生産井があう、安価で
ある利点も有する。As is clear from the above results, the sliding member of the present invention:
It is an excellent sliding member that has excellent adhesion to the base material, strength of the coating layer, wear resistance, and seizure resistance, and has improved the problems of conventional cast or thermal sprayed products. In particular, it can be used in a wide range of applications due to the improved adhesion strength with the base material and the strength of the coating layer. It also has the advantage of being compatible with production wells and being inexpensive.
第１図は本発明法と従来法の工程比較図、第２図は本発
明材と従来材の顕微鏡写真、第３図は本発明の加熱処理
後の顕微鏡写真、第４図１”ｊ３〜２０μｍのＳｉ晶が
全８１晶面積に占める割合と耐摩耗性の関係を示す線図
、第５図は本発明材と比較材の摩耗試験結果を示すグラ
フ、第６図は耐第３ 目
ｊＪ４− 固Fig. 1 is a process comparison diagram of the present invention method and the conventional method, Fig. 2 is a microscopic photograph of the inventive material and the conventional material, Fig. 3 is a microscopic photograph of the present invention after heat treatment, and Fig. 4 is a photomicrograph of the present invention material and the conventional material. A diagram showing the relationship between the ratio of 20 μm Si crystals to the total 81 crystal area and wear resistance, Figure 5 is a graph showing the wear test results of the present invention material and comparative material, and Figure 6 is a graph showing the wear resistance of the 3rd layer jJ4. - hard
Claims (1)
合金を溶融状態から急冷してＳｉの過飽和層を設け、熱
処理と熱間塑性加工を施こし、Ｓｉ晶の平均粒径を３〜
２０μｍの大きさに晶出させたことを特徴とする摺動部
材の製造方法。1. An Al-Si alloy containing hypereutectic Si is rapidly cooled from a molten state on a metal base material to form a supersaturated layer of Si, and heat treatment and hot plastic working are performed to reduce the average grain size of Si crystals to 3. ~
A method for manufacturing a sliding member, characterized in that the crystals are crystallized to a size of 20 μm.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP14034385A JPS621851A (en) | 1985-06-28 | 1985-06-28 | Manufacture of sliding member |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP14034385A JPS621851A (en) | 1985-06-28 | 1985-06-28 | Manufacture of sliding member |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS621851A true JPS621851A (en) | 1987-01-07 |
Family
ID=15266622
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP14034385A Pending JPS621851A (en) | 1985-06-28 | 1985-06-28 | Manufacture of sliding member |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS621851A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0837152A1 (en) * | 1996-10-18 | 1998-04-22 | Bayerische Motoren Werke Aktiengesellschaft, Patentabteilung AJ-3 | Process for coating an aluminium alloy device of an internal combustion engine with silicon |
| DE10313957A1 (en) * | 2002-06-27 | 2004-01-22 | Bwg Gmbh & Co. Kg | Method for coating a surface of a track component and track component |
-
1985
- 1985-06-28 JP JP14034385A patent/JPS621851A/en active Pending
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0837152A1 (en) * | 1996-10-18 | 1998-04-22 | Bayerische Motoren Werke Aktiengesellschaft, Patentabteilung AJ-3 | Process for coating an aluminium alloy device of an internal combustion engine with silicon |
| DE10313957A1 (en) * | 2002-06-27 | 2004-01-22 | Bwg Gmbh & Co. Kg | Method for coating a surface of a track component and track component |
| US7056596B2 (en) | 2002-06-27 | 2006-06-06 | Bwg Gmbh & Co. Kg | Method for coating a surface of a track component, in addition to a track component |
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