JPH04301031A - Steel member excellent in wear resistance and its production - Google Patents
Steel member excellent in wear resistance and its productionInfo
- Publication number
- JPH04301031A JPH04301031A JP6624391A JP6624391A JPH04301031A JP H04301031 A JPH04301031 A JP H04301031A JP 6624391 A JP6624391 A JP 6624391A JP 6624391 A JP6624391 A JP 6624391A JP H04301031 A JPH04301031 A JP H04301031A
- Authority
- JP
- Japan
- Prior art keywords
- graphite
- treatment
- steel member
- wear resistance
- austempering
- 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.)
- Withdrawn
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 47
- 239000010959 steel Substances 0.000 title claims abstract description 47
- 238000004519 manufacturing process Methods 0.000 title claims description 11
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 81
- 229910002804 graphite Inorganic materials 0.000 claims abstract description 76
- 239000010439 graphite Substances 0.000 claims abstract description 76
- 238000005279 austempering Methods 0.000 claims abstract description 42
- 238000001556 precipitation Methods 0.000 claims abstract description 42
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 16
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 16
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 14
- 230000000717 retained effect Effects 0.000 claims abstract description 12
- 229910001562 pearlite Inorganic materials 0.000 claims abstract description 6
- 238000000034 method Methods 0.000 claims description 6
- 239000000203 mixture Substances 0.000 abstract description 11
- 239000000047 product Substances 0.000 description 34
- 230000000052 comparative effect Effects 0.000 description 18
- 238000001816 cooling Methods 0.000 description 11
- 239000000463 material Substances 0.000 description 11
- 229910000677 High-carbon steel Inorganic materials 0.000 description 10
- 229910001141 Ductile iron Inorganic materials 0.000 description 9
- 230000000694 effects Effects 0.000 description 8
- 238000010438 heat treatment Methods 0.000 description 8
- 239000012535 impurity Substances 0.000 description 6
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 6
- 239000002245 particle Substances 0.000 description 6
- 229910052748 manganese Inorganic materials 0.000 description 5
- 230000009466 transformation Effects 0.000 description 5
- 229910052751 metal Inorganic materials 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 3
- 239000003921 oil Substances 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 229920006395 saturated elastomer Polymers 0.000 description 3
- 238000005496 tempering Methods 0.000 description 3
- 229910000838 Al alloy Inorganic materials 0.000 description 2
- 229910000975 Carbon steel Inorganic materials 0.000 description 2
- 238000005299 abrasion Methods 0.000 description 2
- 239000010962 carbon steel Substances 0.000 description 2
- 229910001567 cementite Inorganic materials 0.000 description 2
- 230000003247 decreasing effect Effects 0.000 description 2
- 230000006698 induction Effects 0.000 description 2
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 2
- 238000003825 pressing Methods 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 229910001018 Cast iron Inorganic materials 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 239000010687 lubricating oil Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 230000002093 peripheral effect Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 102200003959 rs11556986 Human genes 0.000 description 1
- 102220259718 rs34120878 Human genes 0.000 description 1
- 102200082816 rs34868397 Human genes 0.000 description 1
- 150000003839 salts Chemical class 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
Landscapes
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
Abstract
Description
【０００１】0001
【産業上の利用分野】本発明は、ＣおよびＳｉの含有量
の比較的多い耐摩耗性の優れた鋼部材およびその製造方
法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a steel member with relatively high C and Si contents and excellent wear resistance, and a method for manufacturing the same.
【０００２】0002
【従来の技術】従来より、例えば球状黒鉛鋳鉄をオース
テンパ処理して熱膨張係数を調整するようにした技術が
、特開昭６１−２５２９１２号公報に見られるように公
知である。2. Description of the Related Art Conventionally, a technique has been known in which, for example, spheroidal graphite cast iron is subjected to austempering treatment to adjust the coefficient of thermal expansion.
【０００３】鋼部材の熱処理は、焼入れ、焼もどし（調
質）が一般的であり、この用途としては通常Ｃ量が０．
４０〜０．５０％の炭素鋼（ＪＩＳ．Ｓ４０Ｃ〜Ｓ５０
Ｃ）または合金鋼が用いられる。しかし、上記のオース
テンパ処理は、通常この調質の代用として或いはその靱
性を改善する目的で行われ、通常の焼入れが鋼のオース
テナイト域の温度から概略室温の焼入れ剤（水、油等）
に急冷する操作であるのに対して、オーステンパ処理は
同じくオーステナイト域から３００ 〜５００ ℃の中
間浴に冷却し、この温度で恒温保持する操作であり、焼
入れに比べて冷却能が小さい。[0003] Heat treatment of steel members generally involves quenching and tempering (refining), and for this purpose, the amount of C is usually 0.
40~0.50% carbon steel (JIS.S40C~S50
C) or alloy steel is used. However, the above-mentioned austempering treatment is usually performed as a substitute for this tempering or for the purpose of improving its toughness.
On the other hand, austempering is an operation in which the austenite region is cooled to an intermediate bath of 300 to 500°C and kept constant at this temperature, and the cooling capacity is smaller than that in quenching.
【０００４】このため、オーステンパ処理は、材料の変
態能を高める必要から調質用途に比べて、炭素量を高め
た鋼材（０．５０〜０．６０％）あるいは、更に炭素含
有量の高い球状黒鉛鋳鉄に適用される。[0004] For this reason, austempering treatment is required to increase the transformation ability of the material, so compared to tempering applications, austempering treatment is used to produce steel materials with a higher carbon content (0.50 to 0.60%) or spherical shapes with an even higher carbon content. Applicable to graphite cast iron.
【０００５】[0005]
【発明が解決しようとする課題】しかして、上記のよう
に炭素含有量の高い高炭素鋼、球状黒鉛鋳鉄にオーステ
ンパ処理を施して用いる場合に対し、さらに耐摩耗性を
高めることが要望される。すなわち、例えば、鋼部材の
熱膨張率を通常の鋼に比べて大きくし、アルミニウム合
金等との熱膨張差を小さくして軸受特性を改善しようと
した際に、その靱性、強度を高めることからオーステン
パ処理を行うについて、その表面部分の耐摩耗性を改善
することは、さらに軸受特性を高める点で好ましいもの
である。[Problem to be Solved by the Invention] However, when high carbon steel with a high carbon content or spheroidal graphite cast iron is used after being austempered, it is desired to further improve the wear resistance. . In other words, for example, when trying to improve bearing characteristics by increasing the coefficient of thermal expansion of steel members compared to normal steel and reducing the difference in thermal expansion with aluminum alloys, etc., it is necessary to increase the toughness and strength of steel members. When carrying out austempering treatment, it is preferable to improve the wear resistance of the surface portion in order to further improve bearing characteristics.
【０００６】特に、球状黒鉛鋳鉄では、炭素量が高くて
組織中に黒鉛が晶出するため、部材の摺動面においては
黒鉛部が油溜りとなることにより、耐摩耗性は高炭素鋼
より良好となる利点を有するが、一方ではこの黒鉛が粗
大であるために弾性率（ヤング率）が低下する問題を有
する。In particular, in spheroidal graphite cast iron, the carbon content is high and graphite crystallizes in the structure, so the graphite portion becomes an oil reservoir on the sliding surface of the member, so its wear resistance is lower than that of high carbon steel. Although this graphite has the advantage of being good, on the other hand, it has the problem that the elastic modulus (Young's modulus) decreases because this graphite is coarse.
【０００７】そこで、本発明は上記事情に鑑み、Ｃ量の
比較的多い鋼部材にオーステンパ処理を施して焼入れ性
を高めると共に、耐摩耗性を改善し、また、ヤング率の
向上を図るようにした耐摩耗性の優れた鋼部材およびそ
の製造方法を提供することを目的とするものである。In view of the above circumstances, the present invention aims to austemper a steel member with a relatively large amount of C to increase hardenability, improve wear resistance, and improve Young's modulus. The object of the present invention is to provide a steel member with excellent wear resistance and a method for manufacturing the same.
【０００８】[0008]
【課題を解決するための手段】上記目的を達成するため
本発明の耐摩耗性の優れた鋼部材の製造方法は、重量％
で、０．６ 〜１．２ ％のＣ、１．０ 〜２．５ ％
のＳｉを含有する鋼部材に、オーステンパ処理を施した
後、黒鉛析出処理を施してなるものである。[Means for Solving the Problems] In order to achieve the above object, the method of manufacturing a steel member with excellent wear resistance of the present invention provides
with 0.6-1.2% C, 1.0-2.5%
A steel member containing Si is subjected to an austempering treatment and then subjected to a graphite precipitation treatment.
【０００９】また、前記黒鉛析出処理をオーステンパ処
理の前に施してもよい。さらに、黒鉛析出処理は、鋼部
材の表面部に局部的に施してもよい。[0009] Furthermore, the graphite precipitation treatment may be performed before the austempering treatment. Furthermore, the graphite precipitation treatment may be applied locally to the surface of the steel member.
【００１０】一方、オーステンパ処理後に黒鉛析出処理
を施してなる耐摩耗性の優れた鋼部材は、内部がベイナ
イトと残留オーステナイトの混在組織であると共に、表
面部は黒鉛が分散したパーライト組織で構成されている
。On the other hand, a steel member with excellent wear resistance that is subjected to graphite precipitation treatment after austempering treatment has a mixed structure of bainite and retained austenite inside, and a pearlite structure in which graphite is dispersed on the surface. ing.
【００１１】また、オーステンパ処理前に黒鉛析出処理
を施してなる耐摩耗性の優れた鋼部材は、内部および表
面部がベイナイトと残留オーステナイトの混在組織であ
り、表面部は黒鉛が分散含有されている。[0011] Furthermore, a steel member with excellent wear resistance that has been subjected to graphite precipitation treatment before austempering treatment has a mixed structure of bainite and retained austenite in the internal and surface areas, and graphite is dispersed in the surface area. There is.
【００１２】上記黒鉛析出処理としては、１１００〜１
２００℃に加熱した後に徐冷する熱処理で行うことが可
能である。また、オーステンパ処理としては、公知の熱
条件で行うことが可能である。[0012] As the graphite precipitation treatment, 1100 to 1
It is possible to perform heat treatment by heating to 200°C and then slowly cooling. Further, the austempering process can be performed under known thermal conditions.
【００１３】[0013]
【作用および効果】上記のような耐摩耗性に優れた鋼部
材およびその製造方法では、比較的多量のＣ，Ｓｉを含
有する鋼部材に対してオーステンパ処理を施す前、もし
くはオーステンパ処理後に、黒鉛析出処理を施して組織
中に微細黒鉛を分散析出させることにより、この黒鉛の
自己潤滑性によって耐摩耗性を向上でき、また、オース
テンパ処理によって靱性、強度の改善が行える。[Operations and Effects] In the above-mentioned steel members with excellent wear resistance and the manufacturing method thereof, graphite is added to steel members containing relatively large amounts of C and Si before or after austempering treatment. By performing precipitation treatment to disperse and precipitate fine graphite in the structure, wear resistance can be improved due to the self-lubricating property of this graphite, and toughness and strength can be improved by austempering treatment.
【００１４】また、特に、オーステンパ処理後に黒鉛析
出処理を施した際には、鋼部材の表面部は黒鉛が分散し
たパーライト組織となって、加工性の改善も得られるも
のである。[0014] In particular, when the graphite precipitation treatment is performed after the austempering treatment, the surface portion of the steel member becomes a pearlite structure in which graphite is dispersed, thereby improving workability.
【００１５】[0015]
【実施例】＜実施例１＞この実施例の耐摩耗性に優れた
鋼部材の製造方法は、鋼部材の局部的（表面）に黒鉛析
出処理を施した後、オーステンパ処理を施してなるもの
である。[Example] <Example 1> The method of manufacturing a steel member with excellent wear resistance in this example is to perform a graphite precipitation treatment locally (on the surface) of the steel member, and then perform an austempering treatment. It is.
【００１６】上記鋼部材の組成は、重量％で、Ｃを０．
６ 〜１．２ ％、Ｓｉを１．０ 〜２．５ ％、Ｍｎ
を０．５ 〜２．０ ％含有し、残部Ｆｅおよび不純物
である。なお、必要に応じてその他の添加元素を含有す
る。The composition of the above-mentioned steel member is 0.0% by weight of C.
6-1.2%, Si 1.0-2.5%, Mn
0.5 to 2.0%, with the remainder being Fe and impurities. Note that other additive elements may be included as necessary.
【００１７】また、比較例として、高炭素鋼では、Ｃを
０．５ 〜０．６％、Ｓｉを０．１５〜０．３５％、Ｍ
ｎを０．６ 〜０．９ ％含有し、残部Ｆｅおよび不純
物である。同様に球状黒鉛鋳鉄では、Ｃを２．５ 〜３
．５ ％、Ｓｉを２．５ ％以下、Ｍｎを０．４ ％以
下含有し、残部Ｆｅおよび不純物である。As a comparative example, high carbon steel contains 0.5 to 0.6% C, 0.15 to 0.35% Si, and M
It contains 0.6 to 0.9% of n, and the remainder is Fe and impurities. Similarly, in spheroidal graphite cast iron, C is 2.5 to 3
．． 5%, Si is 2.5% or less, Mn is 0.4% or less, and the balance is Fe and impurities.
【００１８】そして、上記方法によるオーステンパ処理
後の組織は、内部および表面部の基地はベイナイトと残
留オーステナイトの混在組織であり、表面部にはこの基
地に黒鉛が分散含有されている。その特徴としては耐摩
耗性および弾性率が良好である。The structure after austempering by the above method is a mixed structure of bainite and retained austenite in the matrix in the interior and the surface, and graphite is dispersed in the matrix in the surface. Its characteristics include good wear resistance and elastic modulus.
【００１９】上記鋼部材の化学組成の必須元素の添加量
の範囲を説明すれば、Ｃ量は、オーステンパ処理特性（
ベイナイト変態能）および黒鉛析出処理での黒鉛析出を
行わせるためには、０．６ ％以上の添加が必要で、逆
に、１．２％を越えると、黒鉛が粗大化して不適当であ
る。また、Ｓｉ量は、炭化物生成を抑制し、基地への炭
素固溶量を大きくするため、１．０ ％以上の添加が必
要であり、２．５ ％を越えると効果が飽和すると共に
加工性が劣化するため不適当である。さらに、Ｍｎ量は
、ベイナイト変態能を向上するため、０．５ ％以上の
添加が必要で、２．０ ％を越えると効果が飽和すると
共に、加工性および靱性が劣化するため不適当である。To explain the range of addition amounts of essential elements in the chemical composition of the above-mentioned steel member, the amount of C is determined by the austempering characteristics (
In order to achieve bainite transformation ability) and graphite precipitation in graphite precipitation treatment, it is necessary to add 0.6% or more; conversely, if it exceeds 1.2%, the graphite will become coarse and unsuitable. . In addition, it is necessary to add Si in an amount of 1.0% or more in order to suppress the formation of carbides and increase the amount of carbon solid solution in the matrix, and if it exceeds 2.5%, the effect is saturated and the processability is It is inappropriate because it deteriorates. Furthermore, in order to improve the bainite transformation ability, it is necessary to add Mn in an amount of 0.5% or more; if it exceeds 2.0%, the effect is saturated and workability and toughness deteriorate, which is inappropriate. .
【００２０】なお、その他の鋼部材の化学組成として、
Ｃｒを１．５ ％以下またはＭｏを０．５％以下または
Ｎｉを２．５ ％以下添加することによって、これらの
組成でベイナイト変態能における質量効果を改善しても
よく、特に大物部品においてはその添加が好適である。
ただし、各々上限を越えると効果が飽和し経済性が損な
われる。また、Ｓを０．１５％以下またはＰｂを０．２
％以下添加することによって、被削性を改善するよう
にしても良い。ただし、各々上限を越えると、強度が著
しく低下するものである。[0020] As for the chemical composition of other steel members,
By adding up to 1.5% Cr, up to 0.5% Mo, or up to 2.5% Ni, the mass effect on bainite transformation ability may be improved in these compositions, especially in large parts. Its addition is preferred. However, if the respective upper limits are exceeded, the effect will be saturated and economic efficiency will be impaired. In addition, S is 0.15% or less or Pb is 0.2% or less.
% or less may be added to improve machinability. However, if each exceeds the upper limit, the strength will drop significantly.
【００２１】次に、鋼部材の黒鉛粒径は、好ましくは
５〜２０μｍである。この黒鉛は、切削加工性を改善す
ると共に、摺動面にあっては、油溜りとなることから耐
摩耗性を改善する効果があり、この点からその粒径は
５μｍ以上が有効である。また、２０μｍを越えると、
弾性率および強度が著しく低下して好ましくない。Next, the graphite grain size of the steel member is preferably
It is 5 to 20 μm. This graphite not only improves machinability but also acts as an oil reservoir on sliding surfaces, improving wear resistance.From this point of view, its particle size is
A thickness of 5 μm or more is effective. Also, if it exceeds 20 μm,
This is undesirable because the elastic modulus and strength are significantly reduced.
【００２２】ここで、黒鉛析出処理の条件を示す。鋼部
材をオーステナイト単相域（９６０ 〜１２００℃）、
または、オーステナイトとセメンタイトとの共存域（７
７０ 〜９６０ ℃）に加熱し、この温度域からＡ１
変態点が完全に終了する温度域（６００ ℃以下）まで
に徐々に冷却する。この冷却速度は、０．１ 〜５ ℃
／ｍｉｎ の範囲で行う。この冷却速度は、上記範囲内
で遅いほど析出黒鉛粒径が大きくなり、速くなるほど黒
鉛粒径が小さくなるので必要に応じて適宜調整するもの
である。なお、鋼部材の摺動面などの特定部位に対して
、黒鉛析出処理を施す場合には、高周波誘導加熱などの
局部加熱手段を用いて行うものである。[0022] Here, the conditions for graphite precipitation treatment will be described. Steel members in the austenite single phase region (960 to 1200℃),
Or, the coexistence region of austenite and cementite (7
70 to 960℃), and from this temperature range A1
It is gradually cooled to a temperature range (600°C or lower) where the transformation point is completely completed. This cooling rate is 0.1~5℃
/min. This cooling rate is adjusted appropriately as necessary, since within the above range, the slower the cooling rate, the larger the precipitated graphite particle size becomes, and the faster the cooling rate, the smaller the graphite particle size becomes. In addition, when graphite precipitation treatment is performed on a specific part such as a sliding surface of a steel member, it is performed using local heating means such as high-frequency induction heating.
【００２３】上記の黒鉛析出処理を行って所望の粒径を
有する黒鉛を析出した後のオーステンパ処理の条件を示
す。鋼部材を、オーステナイト単相域（９６０〜１２０
０℃）、または、オーステナイトとセメンタイトとの共
存域（７７０ 〜９６０ ℃）に加熱し、この温度域か
ら３００ 〜５００ ℃の中間浴に急冷し、この温度域
で３０〜３００ ｍｉｎ 保持する。この中間浴の温度
および保持時間によって、オーステンパ処理後の金属組
織におけるベイナイトと残留オーステナイトの構成比が
変わるので必要に応じて適宜調整する。The conditions for the austempering treatment after the above-described graphite precipitation treatment has been performed to precipitate graphite having a desired particle size are shown below. Steel members are made of austenite single phase region (960~120
0°C) or to a coexistence range of austenite and cementite (770 to 960°C), and from this temperature range, rapidly cooled to an intermediate bath of 300 to 500°C, and held in this temperature range for 30 to 300 min. The composition ratio of bainite and retained austenite in the metal structure after austempering changes depending on the temperature and holding time of this intermediate bath, so it is adjusted as necessary.
【００２４】次に、前記黒鉛析出処理による耐摩耗性の
改善効果を確認した試験結果を示す。テスト材の組成は
、本発明鋼部材Ａは、Ｃを０．８５％、Ｓｉを１．７５
％、Ｍｎを１．２５％含有し、残部Ｆｅおよび不純物で
ある。また、比較例Ｂ（高炭素鋼ＪＩＳ．Ｓ５５Ｃ）は
、Ｃを０．５５％、Ｓｉを０．２５％、Ｍｎを０．７５
％含有し、残部Ｆｅおよび不純物である。さらに、比較
例Ｃ（球状黒鉛鋳鉄ＪＩＳ．ＦＣＤ６００）は、Ｃを３
．２５％、Ｓｉを２．２５％、Ｍｎを０．２５％含有し
、残部Ｆｅおよび不純物である。Next, the results of a test confirming the effect of improving wear resistance by the graphite precipitation treatment will be shown. The composition of the test material is that steel member A of the present invention contains 0.85% C and 1.75% Si.
%, contains 1.25% Mn, and the remainder is Fe and impurities. Comparative example B (high carbon steel JIS.S55C) contains 0.55% C, 0.25% Si, and 0.75% Mn.
%, and the remainder is Fe and impurities. Furthermore, Comparative Example C (spheroidal graphite cast iron JIS.FCD600) has C of 3
．． 25% Si, 2.25% Si, 0.25% Mn, and the remainder is Fe and impurities.
【００２５】上記組成の素材を熱間加工後、焼準して、
所定形状の試験片を製作した（本発明品１）。また、本
実施例試験片に施した黒鉛析出処理は、９８０℃に加熱
後、毎分０．５ ℃の冷却速度で６００ ℃まで徐冷し
、以降室温まで空冷した。なお、比較例１は前記Ａの組
成で上記黒鉛析出処理を施していないもの、比較例２が
Ｂの高炭素鋼（黒鉛析出処理なし）で、比較例３がＣの
球状黒鉛鋳鉄（黒鉛析出処理なし）である。そして、上
記テストピースに対して同一条件のオーステンパ処理を
施してなる。このオーステンパ処理は、９００ ℃に加
熱後、４００ ℃の塩浴に急冷し、この温度で １２０
分恒温処理して行った。[0025] After hot working the material having the above composition, normalizing it,
A test piece with a predetermined shape was manufactured (Product 1 of the present invention). Further, the graphite precipitation treatment applied to the test piece of this example was heated to 980°C, then slowly cooled to 600°C at a cooling rate of 0.5°C per minute, and then air-cooled to room temperature. Comparative Example 1 is a high carbon steel with the composition A and not subjected to the graphite precipitation treatment, Comparative Example 2 is a high carbon steel of B (without graphite precipitation treatment), and Comparative Example 3 is a spheroidal graphite cast iron of C (without graphite precipitation treatment). (no processing). The above test piece was then subjected to austempering treatment under the same conditions. This austempering process involves heating to 900°C and then rapidly cooling it in a salt bath at 400°C.
It was subjected to constant temperature treatment for 1 minute.
【００２６】上記オーステンパ処理後の、本発明品１、
比較品１〜３の金属組織の顕微鏡写真を図１、図４〜図
６に示す。図１の本発明品１で３カ所に黒く点在してい
る斑点状のものが析出した黒鉛である。この本発明品１
と同材質でも黒鉛析出処理のない比較品１（図４）では
黒鉛は析出しておらず、同様に比較品２（図５）の高炭
素鋼でも黒鉛は析出していない。また、比較品３（図６
）の球状黒鉛鋳鉄では黒鉛析出処理を施していなくても
大径の黒鉛が晶出している。[0026] Product 1 of the present invention after the austempering treatment,
Microscopic photographs of the metal structures of Comparative Products 1 to 3 are shown in FIGS. 1 and 4 to 6. In the product 1 of the present invention shown in FIG. 1, the black spots scattered at three locations are precipitated graphite. This invention product 1
Comparative product 1 (FIG. 4), which is made of the same material but without graphite precipitation treatment, does not have graphite precipitated, and similarly, graphite does not precipitate in the high carbon steel of comparative product 2 (FIG. 5). In addition, comparative product 3 (Fig. 6
), large-diameter graphite crystallizes even without graphite precipitation treatment.
【００２７】耐摩耗テストは、前記テストピースを回転
円板に押し付けながら摺動させ、徐々に押し付け荷重を
増加させて焼付き（異常摩耗）が発生した時点の荷重の
大きさによって耐摩耗性を評価した。上記テストピース
の形状は、幅×高さ×厚さが８．５ｍｍ× ５ｍｍ×
３ｍｍの部材の上端面に半径 ２ｍｍの円弧テスト面を
形成してなり、この円弧面を円板に押圧して摩耗量を測
定する。なお、円板の材質は炭素鋼調質材（Ｓ４５Ｃ、
硬さＨｖ３００ ）で、摺動速度は２０ｍ／ｓｅｃ で
ある。また、潤滑油は１０Ｗ３０を使用し、給油量は３
００ｃｃ／ｍｉｎ とした。In the wear resistance test, the test piece is slid while being pressed against a rotating disk, the pressing load is gradually increased, and the wear resistance is evaluated depending on the magnitude of the load at the time when seizure (abnormal wear) occurs. evaluated. The shape of the above test piece is width x height x thickness 8.5mm x 5mm x
An arcuate test surface with a radius of 2mm is formed on the upper end surface of a 3mm member, and the amount of wear is measured by pressing this arcuate surface against a disc. The material of the disc is carbon steel tempered material (S45C,
The hardness is Hv300) and the sliding speed is 20 m/sec. In addition, 10W30 lubricating oil is used, and the amount of oil supplied is 3
00cc/min.
【００２８】上記耐摩耗テストの結果およびオーステン
パ処理後の表面硬度を表１に示す。このテスト結果から
、オーステンパ処理を施すことにより各テストピース共
に表面硬度が高くなっているが、本発明品１では、前記
黒鉛析出処理を施していることから、この析出黒鉛の影
響で耐摩耗性が比較品３の球状黒鉛鋳鉄と同等に良好な
耐摩耗性が得られた。なお、黒鉛析出処理を施していな
い比較品１では、高炭素鋼より若干良い程度の耐摩耗性
を示している。また、本発明品２，３は、後述の実施例
３の試験片のデータである。Table 1 shows the results of the above wear resistance test and the surface hardness after austempering. From this test result, the surface hardness of each test piece is increased by applying the austempering treatment, but since the graphite precipitation treatment is applied to the product 1 of the present invention, the wear resistance is improved due to the influence of this precipitated graphite. However, the same good wear resistance as Comparative Product 3, spheroidal graphite cast iron, was obtained. Note that Comparative Product 1, which was not subjected to graphite precipitation treatment, exhibited slightly better wear resistance than high carbon steel. Moreover, the present invention products 2 and 3 are the data of the test piece of Example 3, which will be described later.
【００２９】[0029]
【表１】[Table 1]
【００３０】さらに、上記オーステンパ処理後の各テス
トピースの弾性率を測定した結果を表２に示す。この弾
性率は、比較品２の高炭素鋼が最も高い値を示し、本発
明品１と同材質の比較品１が次に高い値を示し、本発明
品１は黒鉛析出処理を施したことによって若干弾性率が
低下しているが、比較品３の球状黒鉛鋳鉄に比べて高い
弾性率を有しているものである。Furthermore, Table 2 shows the results of measuring the elastic modulus of each test piece after the austempering treatment. Regarding this elastic modulus, Comparative Product 2, high carbon steel, showed the highest value, and Comparative Product 1, which is made of the same material as Inventive Product 1, showed the next highest value, and Inventive Product 1 was subjected to graphite precipitation treatment. Although the elastic modulus is slightly lowered due to this, it has a higher elastic modulus than Comparative Product 3, which is spheroidal graphite cast iron.
【００３１】[0031]
【表２】[Table 2]
【００３２】＜実施例２＞この実施例の耐摩耗性の優れ
た鋼部材の製造方法は、鋼部材にオーステンパ処理を施
した後に、黒鉛析出処理を施してなるものである。<Example 2> The method of manufacturing a steel member with excellent wear resistance according to this example is to perform a graphite precipitation treatment on a steel member after austempering treatment.
【００３３】上記鋼部材の組成は、前例と同様であり、
添加量の範囲も同様である。そして、この方法による処
理後の組織は、内部がベイナイトと残留オーステナイト
の混在組織であると共に、黒鉛析出処理を施した表面部
は微細黒鉛が分散したパーライト組織またはベイナイト
組織である。そして、その特徴とするところは、耐摩耗
性および弾性率が良好であると共に、表面部の熱膨張率
が前例の場合より小さくなっている。[0033] The composition of the above steel member is the same as that of the previous example,
The range of addition amount is also the same. The structure after treatment by this method has a mixed structure of bainite and retained austenite inside, and a pearlite structure or bainite structure in which fine graphite is dispersed on the surface portion subjected to graphite precipitation treatment. Its characteristics include good abrasion resistance and elastic modulus, and a lower coefficient of thermal expansion at the surface than in the previous example.
【００３４】また、オーステンパ処理は、前例と同様で
あり、鋼部材を７７０〜１２００℃に加熱し、３００
〜５００ ℃の中間浴に急冷して、３０〜３００ ｍｉ
ｎ 保持するものである。
さらに、このオーステンパ処理の後に施す黒鉛析出処理
の条件についても前例と同様であり、鋼部材を７７０
〜１２００℃に加熱し、この温度域から６００ ℃以下
に、０．１ 〜５ ℃／ｍｉｎ の冷却速度で徐冷する
ものである。[0034] Also, the austempering treatment is the same as in the previous example, in which the steel member is heated to 770 to 1200°C and heated to 300°C.
Rapid cooling in an intermediate bath of ~500 °C for 30–300 mi
n to be retained. Furthermore, the conditions for the graphite precipitation treatment performed after this austempering treatment are also the same as in the previous example, and the steel member is
It is heated to ~1200°C, and slowly cooled from this temperature range to 600°C or less at a cooling rate of 0.1 to 5°C/min.
【００３５】この実施例によれば、オーステンパ処理後
に黒鉛析出処理を施すことにより前例同様の耐摩耗性の
の改善効果が得られる一方、表面部の基地がパーライト
に黒鉛が分散していることで、加工性も向上するもので
ある。According to this example, by performing graphite precipitation treatment after austempering treatment, the same effect of improving wear resistance as in the previous example can be obtained. , processability is also improved.
【００３６】＜実施例３＞この実施例の耐摩耗性の優れ
た鋼部材の製造方法は、鋼部材にオーステンパ処理の前
もしくは後に局部黒鉛析出処理を施してなるものである
。<Example 3> The method of manufacturing a steel member with excellent wear resistance according to this example is to subject a steel member to localized graphite precipitation treatment before or after austempering treatment.
【００３７】本発明品２は、実施例１の本発明品１と同
一の組成で、形状は直径３０ｍｍの棒材であり、局部黒
鉛析出処理の後にオーステンパ処理を施したものである
。また、本発明品３は、同じ素材に、オーステンパ処理
を行った後に局部黒鉛析出処理を施したものである。Inventive product 2 has the same composition as inventive product 1 of Example 1, is a bar with a diameter of 30 mm, and is subjected to local graphite precipitation treatment followed by austempering treatment. Inventive product 3 is obtained by subjecting the same material to local graphite precipitation treatment after austempering treatment.
【００３８】上記局部黒鉛析出処理は、素材の外周面を
表面下 ３ｍｍまで高周波誘導加熱により ８５０℃に
加熱した後、この部位の温度が ６００℃になるまで加
熱出力を漸減させながら ５℃／ｍｉｎの冷却速度で徐
冷し、以降室温まで空冷して行う。また、オーステンパ
処理は、実施例１と同条件である。[0038] In the above-mentioned local graphite precipitation treatment, the outer peripheral surface of the material is heated to 850°C by high-frequency induction heating up to 3mm below the surface, and then heated at 5°C/min while gradually decreasing the heating output until the temperature of this part reaches 600°C. Cool slowly at a cooling rate of , and then air cool to room temperature. Further, the austempering treatment was performed under the same conditions as in Example 1.
【００３９】局部黒鉛析出処理の後にオーステンパ処理
を行った本発明品２の金属組織の顕微鏡写真を図２に示
し、その局部処理により黒色の黒鉛が析出し、黒鉛粒径
は約１０μｍである。一方、オーステンパ処理の後に局
部黒鉛析出処理を行った本発明品３の金属組織の顕微鏡
写真を図３に示し、その局部処理により黒鉛が点在し黒
鉛粒径は約５μｍである。FIG. 2 shows a microscopic photograph of the metal structure of product 2 of the present invention, which was subjected to austempering treatment after local graphite precipitation treatment. Black graphite was precipitated by the local treatment, and the graphite particle size was about 10 μm. On the other hand, FIG. 3 shows a microscopic photograph of the metal structure of product 3 of the present invention, which was subjected to localized graphite precipitation treatment after austempering treatment. As a result of the localized treatment, graphite was scattered and the graphite particle size was about 5 μm.
【００４０】上記本発明品２および３に対して実施例１
と同じ要領の耐摩耗テストと行った結果および測定した
表面硬度を前記表１に併記し、さらに、弾性率および熱
膨張量を測定した結果を前記表２に示している。熱膨張
量の測定は、試料の外径（３０ｍｍ）を室温および ２
００℃で測定し、各々の差を算出したものである。なお
、前記比較品１〜３の熱膨張量についても表２に示す。Example 1 for the above invention products 2 and 3
The results of the abrasion resistance test conducted in the same manner as above and the measured surface hardness are also listed in Table 1 above, and the results of measuring the elastic modulus and amount of thermal expansion are also shown in Table 2 above. To measure the amount of thermal expansion, measure the outer diameter of the sample (30 mm) at room temperature and 2
Measurements were taken at 00°C and the differences between each were calculated. In addition, Table 2 also shows the amount of thermal expansion of the comparative products 1 to 3.
【００４１】上記のような本発明品２および３は、前述
のように摺動面に黒鉛が析出していることにより、本発
明品１および比較品３（球状黒鉛鋳鉄）と同等の耐摩耗
性が得られている。また、黒鉛析出層が表面に限られて
いることにより、同質材の比較品１に対して弾性率の低
下もごくわずかであった。この本発明品２と本発明品３
との相違点は、本発明品２の局部処理部分が微細黒鉛の
析出したベイナイト＋残留オーステナイト組織であるの
に対し、本発明品３の局部処理部分は、基地の残留オー
ステナイトが分解したパーライト組織となっている点で
ある。これにより、本発明品３の方が熱膨張率が小さく
なっている。Inventive products 2 and 3 as described above have the same wear resistance as inventive product 1 and comparative product 3 (spheroidal graphite cast iron) because graphite is precipitated on the sliding surface as described above. sex is obtained. Furthermore, since the graphite precipitated layer was limited to the surface, the elastic modulus decreased only slightly compared to Comparative Product 1 made of the same material. This invention product 2 and this invention product 3
The difference is that the locally treated part of Inventive Product 2 has a bainite + retained austenite structure in which fine graphite precipitates, whereas the locally treated part of Inventive Product 3 has a pearlite structure in which retained austenite in the base is decomposed. This is the point. As a result, the thermal expansion coefficient of Invention Product 3 is smaller than that of Invention Product 3.
【００４２】また、上記ような本発明の製造方法による
鋼部材は、通常の高炭素鋼に比べて熱膨張係数が大きく
なり、アルミニウム合金等との熱膨張差を小さくして軸
受特性を改善できる作用を有する。[0042] Furthermore, the steel member produced by the manufacturing method of the present invention as described above has a larger coefficient of thermal expansion than ordinary high carbon steel, and can improve bearing characteristics by reducing the difference in thermal expansion with aluminum alloy, etc. It has an effect.
Claims (5)
、１．０ 〜２．５ ％のＳｉを含有する鋼部材に、オ
ーステンパ処理を施した後、黒鉛析出処理を施すことを
特徴とする耐摩耗性の優れた鋼部材の製造方法。Claim 1: 0.6 to 1.2% C by weight%
, 1.0 to 2.5% of Si is subjected to an austempering treatment and then subjected to a graphite precipitation treatment.
がオーステンパ処理の前に施されることをことを特徴と
する耐摩耗性の優れた鋼部材の製造方法。2. The method of manufacturing a steel member having excellent wear resistance according to claim 1, wherein the graphite precipitation treatment is performed before the austempering treatment.
にのみ施されることを特徴とする請求項１または２記載
の耐摩耗性の優れた鋼部材の製造方法。3. The method for manufacturing a steel member with excellent wear resistance according to claim 1 or 2, wherein the graphite precipitation treatment is applied only to a surface portion of the steel member.
、１．０ 〜２．５ ％のＳｉを含有する鋼部材にオー
ステンパ処理と黒鉛析出処理を施し、内部がベイナイト
と残留オーステナイトの混在組織で、表面部は黒鉛が分
散したパーライト組織であることを特徴とする耐摩耗性
の優れた鋼部材。4. 0.6 to 1.2% C by weight%
, a steel member containing 1.0 to 2.5% Si was subjected to austempering treatment and graphite precipitation treatment, and it was found that the interior was a mixed structure of bainite and retained austenite, and the surface was a pearlite structure with dispersed graphite. A steel component with excellent wear resistance.
、１．０ 〜２．５ ％のＳｉを含有する鋼部材にオー
ステンパ処理と黒鉛析出処理を施し、内部および表面部
がベイナイトと残留オーステナイトの混在組織であり、
表面部は黒鉛が分散含有されていることを特徴とする耐
摩耗性の優れた鋼部材。5. 0.6 to 1.2% C by weight%
, a steel member containing 1.0 to 2.5% Si is subjected to austempering treatment and graphite precipitation treatment, and the internal and surface parts have a mixed structure of bainite and retained austenite,
A steel member with excellent wear resistance characterized by graphite being dispersed on the surface.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6624391A JPH04301031A (en) | 1991-03-29 | 1991-03-29 | Steel member excellent in wear resistance and its production |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6624391A JPH04301031A (en) | 1991-03-29 | 1991-03-29 | Steel member excellent in wear resistance and its production |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH04301031A true JPH04301031A (en) | 1992-10-23 |
Family
ID=13310234
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP6624391A Withdrawn JPH04301031A (en) | 1991-03-29 | 1991-03-29 | Steel member excellent in wear resistance and its production |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH04301031A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6884306B1 (en) | 1999-08-04 | 2005-04-26 | Qinetiq Limited | Baintic steel |
| JP2009235444A (en) * | 2008-03-26 | 2009-10-15 | Ntn Corp | Method for applying heat-treatment for steel, method for manufacturing machine part, machine part, and rolling bearing |
-
1991
- 1991-03-29 JP JP6624391A patent/JPH04301031A/en not_active Withdrawn
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6884306B1 (en) | 1999-08-04 | 2005-04-26 | Qinetiq Limited | Baintic steel |
| JP2009235444A (en) * | 2008-03-26 | 2009-10-15 | Ntn Corp | Method for applying heat-treatment for steel, method for manufacturing machine part, machine part, and rolling bearing |
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Free format text: JAPANESE INTERMEDIATE CODE: A300 Effective date: 19980514 |