JP2012207247A - Carburizing member, steel for carburizing member and method for producing carburizing member - Google Patents
Carburizing member, steel for carburizing member and method for producing carburizing member Download PDFInfo
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本発明は、浸炭部材、浸炭部材用鋼および浸炭部材の製造方法に関する。 The present invention relates to a carburized member, steel for carburized member, and a method for manufacturing a carburized member.
鋼材は、使用目的によって、表面だけを硬質で耐摩耗性のある状態にする一方、中心部分を柔軟性と靱性に富む状態にして用いられることがある。このような鋼材の用途としては、例えば、ベルト式無段変速機(以下、「ベルト式CVT」という。)のプーリーを構成するCVTシーブなどがある。この種のCVTシーブは、金属ベルトと常に摺動する摺動面を有しており、その摺動面には高い耐摩耗性が要求される。 Depending on the purpose of use, the steel material may be used with only the surface being hard and wear-resistant, while the central portion is rich in flexibility and toughness. As an application of such a steel material, for example, there is a CVT sheave constituting a pulley of a belt type continuously variable transmission (hereinafter referred to as “belt type CVT”). This type of CVT sheave has a sliding surface that always slides with the metal belt, and the sliding surface is required to have high wear resistance.
従来、鋼材の表面硬化法としては、浸炭焼入れ処理が知られている。浸炭焼入れ処理は、加工性のよい低炭素鋼を機械加工等した後、表層の炭素量を増加させ、表層のみを焼入れ硬化させる処理である。これまで、上記CVTシーブ等の鋼部材に耐摩耗性を付与するため、浸炭焼入れ処理が施されてきた。 Conventionally, carburizing and quenching is known as a surface hardening method for steel materials. The carburizing and quenching process is a process of increasing the amount of carbon in the surface layer and quenching and hardening only the surface layer after machining low carbon steel with good workability. In the past, carburizing and quenching has been performed to impart wear resistance to steel members such as the CVT sheave.
また他にも、耐摩耗性を向上させるため、上記浸炭焼入れ処理後、さらにショットピーニング処理を追加して表面硬さや残留応力を向上させる技術や、高濃度浸炭処理によって微細炭化物を分散させるという組織的な改善技術や、研磨方法を工夫して表面粗さを耐摩耗性に好適な状態に改善する技術なども提案されている(特許文献1〜4)。
In addition, in order to improve wear resistance, after the above carburizing and quenching treatment, a technique that further adds shot peening treatment to improve surface hardness and residual stress, and a structure that fine carbide is dispersed by high concentration carburizing treatment A technique for improving the surface roughness to a state suitable for wear resistance by devising a general improvement technique or a polishing method has been proposed (
しかしながら、従来技術は、以下の点で問題がある。すなわち、ショットピーニング等の追加処理はコストアップを伴う。そのため、この種の追加処理を施すことなく、浸炭部材の耐摩耗性向上を図りたいという要請がある。とりわけ、自動車用部品の一つであるCVTシーブは、コスト低減要求が厳しい。そのため、浸炭焼入れ処理のほかに特別な表面処理を追加せずに摺動面の耐摩耗性を改善する方法が求められている。 However, the prior art has problems in the following points. That is, additional processing such as shot peening involves an increase in cost. Therefore, there is a demand to improve the wear resistance of the carburized member without performing this kind of additional processing. In particular, CVT sheaves, which are one of automotive parts, have severe demands for cost reduction. Therefore, there is a demand for a method for improving the wear resistance of the sliding surface without adding a special surface treatment in addition to the carburizing and quenching treatment.
本発明は、このような問題に鑑みてなされたものであり、大幅なコストアップを伴うことなく耐摩耗性を向上させることが可能な浸炭部材を提供しようとするものである。また、上記浸炭部材の半製品である浸炭部材用鋼を提供しようとするものである。また、上記浸炭部材の製造方法を提供しようとするものである。 The present invention has been made in view of such problems, and an object of the present invention is to provide a carburized member capable of improving the wear resistance without significantly increasing the cost. Moreover, it is going to provide the steel for carburized members which is a semi-finished product of the said carburized member. Moreover, it is going to provide the manufacturing method of the said carburized member.
第1の発明は、摺動面を有する浸炭部材であって、
化学成分が、質量%で、C:0.10〜0.30%、Si:0.50〜2.00%、Mn:0.30〜1.50%、P:0.035%以下、S:0.035%以下、Cr:1.35〜3.00%、Al:0.020〜0.060%、および、N:0.0080〜0.0250%を含有し、残部がFeおよび不可避不純物よりなり、
上記摺動面は、浸炭異常層がなく、表面炭素濃度が0.7〜0.9質量%の範囲内にあり、最表面からの深さ50μmまでにおける組織のトルースタイト面積率が1%以下であることを特徴とする浸炭部材にある(請求項1)。
The first invention is a carburized member having a sliding surface,
Chemical component is mass%, C: 0.10 to 0.30%, Si: 0.50 to 2.00%, Mn: 0.30 to 1.50%, P: 0.035% or less, S : 0.035% or less, Cr: 1.35 to 3.00%, Al: 0.020 to 0.060%, and N: 0.0080 to 0.0250%, the balance being Fe and inevitable Consisting of impurities,
The sliding surface has no carburized abnormal layer, the surface carbon concentration is in the range of 0.7 to 0.9 mass%, and the troostite area ratio of the structure at a depth of 50 μm from the outermost surface is 1% or less. It is in the carburized member characterized by being (claim 1).
第2の発明は、摺動面を有し、該摺動面は、浸炭異常層がなく、表面炭素濃度が0.7〜0.9質量%の範囲内にあり、最表面からの深さ50μmまでにおける組織のトルースタイト面積率が1%以下である浸炭部材を製造するために用いられる浸炭部材用鋼であって、
化学成分が、質量%で、C:0.10〜0.30%、Si:0.50〜2.00%、Mn:0.30〜1.50%、P:0.035%以下、S:0.035%以下、Cr:1.35〜3.00%、Al:0.020〜0.060%、および、N:0.0080〜0.0250%を含有し、残部がFeおよび不可避不純物よりなることを特徴とする浸炭部材用鋼にある(請求項4)。
2nd invention has a sliding surface, this sliding surface has no carburizing abnormal layer, surface carbon concentration exists in the range of 0.7-0.9 mass%, and depth from outermost surface. A carburized member steel used for producing a carburized member having a structure troostite area ratio of up to 50 μm of 1% or less,
Chemical component is mass%, C: 0.10 to 0.30%, Si: 0.50 to 2.00%, Mn: 0.30 to 1.50%, P: 0.035% or less, S : 0.035% or less, Cr: 1.35 to 3.00%, Al: 0.020 to 0.060%, and N: 0.0080 to 0.0250%, the balance being Fe and inevitable It is in the steel for carburized members which consists of impurities (Claim 4).
第3の発明は、鋼部材に炭素を侵入させる浸炭期と上記鋼部材に侵入した炭素を拡散させる拡散期とを備えた浸炭処理工程と、該浸炭処理工程を経た鋼部材を焼入れする焼入工程とを有する浸炭部材の製造方法であって、
上記鋼部材は、化学成分が、質量%で、C:0.10〜0.30%、Si:0.50〜2.00%、Mn:0.30〜1.50%、P:0.035%以下、S:0.035%以下、Cr:1.35〜3.00%、Al:0.020〜0.060%、および、N:0.0080〜0.0250%を含有し、残部がFeおよび不可避不純物よりなり、
上記浸炭期におけるカーボンポテンシャルは1.3%以上とされることを特徴とする浸炭部材の製造方法にある(請求項6)。
According to a third aspect of the invention, there is provided a carburizing process including a carburizing period in which carbon enters a steel member and a diffusion period in which carbon invading the steel member is diffused, and quenching the steel member that has undergone the carburizing process. A carburized member manufacturing method comprising:
The steel member has a chemical composition of mass%, C: 0.10 to 0.30%, Si: 0.50 to 2.00%, Mn: 0.30 to 1.50%, P: 0.00. 035% or less, S: 0.035% or less, Cr: 1.35 to 3.00%, Al: 0.020 to 0.060%, and N: 0.0080 to 0.0250%, The balance consists of Fe and inevitable impurities,
The carbon potential in the carburizing period is 1.3% or more.
第1の発明の浸炭部材は、上記特定の化学成分を有し、上記摺動面は、浸炭異常層がなく、表面炭素濃度が0.7〜0.9質量%の範囲内にあり、最表面からの深さ50μmまでにおける組織のトルースタイト面積率が1%以下である。そのため、大幅なコストアップを伴うショットピーニング等の追加処理を施さなくても、摺動面の耐摩耗性に優れる。 The carburized member of the first invention has the above-mentioned specific chemical component, the sliding surface has no carburized abnormal layer, and the surface carbon concentration is in the range of 0.7 to 0.9% by mass. The troostite area ratio of the structure at a depth of 50 μm from the surface is 1% or less. For this reason, the wear resistance of the sliding surface is excellent even without additional processing such as shot peening with a significant cost increase.
第2の発明の浸炭部材用鋼は、上記浸炭部材を製造するために用いられる鋼であって、上記特定の化学成分を有する。また、第3の発明の浸炭部材の製造方法は、上記特定の化学成分を有する鋼から構成される鋼部材に対して浸炭処理を行うにあたり、浸炭処理時の浸炭期におけるカーボンポテンシャルを1.3%以上とする。 The steel for carburized member of the second invention is steel used for producing the carburized member and has the specific chemical component. Further, in the method for producing a carburized member of the third invention, when carburizing the steel member composed of the steel having the specific chemical component, the carbon potential in the carburizing period at the time of carburizing is set to 1.3. % Or more.
Si、Cr含有量を増加させると、浸炭性が阻害されるため、このような鋼材は、浸炭部材用鋼としては不向きであった。しかし、Si含有量が0.50%以上、Cr含有量が1.35%以上と比較的高い含有量の場合であっても、浸炭処理時の浸炭期におけるカーボンポテンシャルを1.3%以上とすれば、浸炭性が確保されることにより浸炭部材の浸炭表層におけるトルースタイトの発生を抑制しつつ、耐摩耗性を向上させることができる。また、Si含有量を0.50〜2.00%と増加させたことによって熱による軟化抵抗が高まり、さらに、Cr含有量を1.35〜3.00%と増加させたことにより浸炭表層のトルースタイトの生成が抑制され、その分、耐摩耗性を向上させることができる。上記特定の化学成分を有する鋼を用いるとともに、浸炭処理時の浸炭期におけるカーボンポテンシャルを1.3%以上として浸炭部材の製造を行えば、大幅なコストアップを伴うことなく摺動面等の耐摩耗性が必要な部位の耐摩耗性を向上させることが可能になることは、本発明の完成によって初めて導き出されたものである。 When the Si and Cr contents are increased, the carburizing property is hindered, and thus such a steel material is unsuitable as a carburized member steel. However, even when the Si content is 0.50% or more and the Cr content is 1.35% or more, the carbon potential in the carburizing period during the carburizing process is 1.3% or more. If it does so, wear resistance can be improved, suppressing generation | occurrence | production of troostite in the carburizing surface layer of a carburizing member by ensuring carburizing property. Further, the softening resistance due to heat is increased by increasing the Si content to 0.50 to 2.00%, and further, the carburized surface layer is increased by increasing the Cr content to 1.35 to 3.00%. The generation of troostite is suppressed, and the wear resistance can be improved accordingly. If steels with the above-mentioned specific chemical components are used, and carburized parts are manufactured with a carbon potential at the carburizing stage of carburizing treatment of 1.3% or more, the resistance to sliding surfaces and the like will not increase significantly. It has been derived for the first time by the completion of the present invention that it becomes possible to improve the wear resistance of a part requiring wear.
このように、本発明によれば、大幅なコストアップを伴うことなく耐摩耗性を向上させることが可能な浸炭部材、これの半製品である浸炭部材用鋼、浸炭部材の製造方法を提供することができる。 Thus, according to the present invention, there are provided a carburized member capable of improving wear resistance without significant cost increase, a steel for carburized member which is a semi-finished product thereof, and a method for manufacturing the carburized member. be able to.
上記浸炭部材、上記浸炭部材用鋼および上記浸炭部材の製造方法における化学成分は、上記のように、質量%で、C:0.10〜0.30%、Si:0.50〜2.00%、Mn:0.30〜1.50%、P:0.035%以下、S:0.035%以下、Cr:1.35〜3.00%、Al:0.020〜0.060%、および、N:0.0080〜0.0250%を含有し、残部がFeおよび不可避不純物よりなる。また、上記化学成分は、Mo:0.80%以下を任意に含有しうる(請求項2、請求項5、請求項7)。以下に、各成分の限定理由につき説明する。なお、上記化学成分は、浸炭表層部分を除いた鋼内部における母材の化学成分である。
The chemical components in the carburized member, the steel for carburized member, and the method for producing the carburized member are, as described above, mass%, C: 0.10 to 0.30%, Si: 0.50 to 2.00. %, Mn: 0.30 to 1.50%, P: 0.035% or less, S: 0.035% or less, Cr: 1.35 to 3.00%, Al: 0.020 to 0.060% And N: 0.0080 to 0.0250%, with the balance being Fe and inevitable impurities. Moreover, the said chemical component can contain Mo: 0.80% or less arbitrarily (
C:0.10〜0.30%
Cは、強度を確保するための基本元素であり、CVTシーブ等の浸炭部材において十分な内部硬さを確保するために、0.10%以上添加する。添加量が多くなりすぎると被削性、冷間鍛造性が低下するため、C含有量の上限を0.30%とする。
C: 0.10 to 0.30%
C is a basic element for ensuring strength, and is added in an amount of 0.10% or more in order to ensure sufficient internal hardness in a carburized member such as a CVT sheave. If the amount added is too large, the machinability and cold forgeability are lowered, so the upper limit of the C content is 0.30%.
Si:0.50〜2.00%
Siは、熱による軟化抵抗性を高めるのに有効な元素であり、その特性を確保するために0.50%以上添加する。Si含有量が多くなりすぎると靱性や加工性が劣化してくるため、Si含有量の上限を2.00%とする。Si含有量の上限は、好ましくは、1.50%であるとよい。
Si: 0.50 to 2.00%
Si is an element effective for enhancing the resistance to softening by heat, and 0.50% or more is added in order to ensure the characteristics. If the Si content is too high, toughness and workability deteriorate, so the upper limit of the Si content is 2.00%. The upper limit of the Si content is preferably 1.50%.
Mn:0.30〜1.50%
Mnは、強度向上に有効な元素であり、CVTシーブ等の浸炭部材において十分な内部硬さを確保するために、0.30%以上添加する。Mnの添加量が多くなりすぎると被削性の低下や、残留オーステナイトの増加による硬さ低下が懸念されるため、Mn含有量の上限を1.50%とする。
Mn: 0.30 to 1.50%
Mn is an element effective for improving the strength, and is added in an amount of 0.30% or more in order to ensure sufficient internal hardness in a carburized member such as a CVT sheave. If the amount of Mn added is too large, the machinability may decrease or the hardness may decrease due to an increase in retained austenite. Therefore, the upper limit of the Mn content is set to 1.50%.
P:0.035%以下
Pは、結晶粒界に偏析して疲労強度を低下させるため、P含有量の上限を0.035%とする。Pは製造上の不純物として不可避に含有される元素であるが、精錬により極力低減することが好ましい。
P: 0.035% or less P is segregated at the grain boundaries to reduce fatigue strength, so the upper limit of the P content is 0.035%. P is an element inevitably contained as an impurity in production, but it is preferable to reduce it as much as possible by refining.
S:0.035%以下
Sは、被削性向上に有効であるが、特に積極添加する必要がない任意元素である。S含有量が多くなりすぎると疲労破壊起点となって強度低下を招く。そのため、S含有量の上限を0.035%とする。
S: 0.035% or less S is an optional element that is effective in improving machinability, but does not need to be particularly positively added. If the S content is too large, it becomes a fatigue fracture starting point and causes a decrease in strength. Therefore, the upper limit of S content is 0.035%.
Cr:1.35〜3.00%
Crは、強度向上に有効な元素であり、CVTシーブ等の浸炭部材において十分な内部硬さを確保するのに役立つ。また、上述の浸炭処理時の浸炭期におけるカーボンポテンシャルを1.3%以上とし、浸炭表層において十分な浸炭濃度を確保することにより、浸炭部材におけるトルースタイトの発生が抑制され、耐摩耗性の向上に有効である。そのため、Crを1.35%以上添加する。Crの添加量が多くなりすぎると硬さが高くなって加工性が低下するため、Cr含有量の上限を3.00%とする。Cr含有量の上限は、好ましくは、2.00%であるとよい。
Cr: 1.35 to 3.00%
Cr is an element effective for improving the strength, and helps to ensure sufficient internal hardness in a carburized member such as a CVT sheave. In addition, by setting the carbon potential in the carburizing period during the carburizing process described above to 1.3% or more and ensuring a sufficient carburizing concentration in the carburized surface layer, generation of troostite in the carburized member is suppressed, and wear resistance is improved. It is effective for. Therefore, 1.35% or more of Cr is added. If the amount of Cr added is too large, the hardness increases and the workability decreases, so the upper limit of the Cr content is 3.00%. The upper limit of the Cr content is preferably 2.00%.
Al:0.020〜0.060%
Alは、脱酸処理に必要なだけでなく、浸炭処理後の結晶粒の粗大化防止効果を得るために有効な元素であり、この効果を得るために0.020%以上添加する。Alの含有量が多くなりすぎるとその効果が飽和するとともに酸化物系介在物の増加によって疲労強度が低下するため、Al含有量の上限を0.060%とする。
Al: 0.020 to 0.060%
Al is an element that is not only necessary for the deoxidation treatment but also effective for obtaining the effect of preventing the coarsening of the crystal grains after the carburizing treatment. To obtain this effect, 0.020% or more is added. If the Al content is excessively increased, the effect is saturated and the fatigue strength is reduced due to an increase in oxide inclusions. Therefore, the upper limit of the Al content is set to 0.060%.
N:0.0080〜0.0250%
Nは、製造上不可避に含有される元素であるが、Alと同様に、結晶粒の粗大化防止に有効であるため、この効果を得るために0.0080%以上含有するように調整して製造する。N含有量が多くなりすぎるとその効果が飽和するとともに窒化物が増加して疲労強度低下の原因となるため、N含有量の上限を0.0250%とする。
N: 0.0080 to 0.0250%
N is an element that is inevitably contained in the production, but, like Al, it is effective in preventing the coarsening of crystal grains. Therefore, in order to obtain this effect, N is adjusted to contain 0.0080% or more. To manufacture. If the N content is excessively increased, the effect is saturated and the nitride increases to cause a decrease in fatigue strength. Therefore, the upper limit of the N content is set to 0.0250%.
Mo:0.80%以下
Moは、上記化学成分に任意に含有可能な元素である。Moは、強度、靱性を向上させるのに有効な元素ではあるが、高価であるため、上限を0.80%に抑える。Mo含有量は、省資源化・低コスト化の観点から、好ましくは、不純物程度であるとよい。
Mo: 0.80% or less Mo is an element that can be optionally contained in the chemical component. Mo is an element effective for improving the strength and toughness, but is expensive, so the upper limit is suppressed to 0.80%. The Mo content is preferably about an impurity from the viewpoint of resource saving and cost reduction.
次に、上記浸炭部材は、他の部材と摺動する摺動面を有している。この種の浸炭部材としては、例えば、CVTシーブ、アウター・インナーレース類、歯車などを例示することができる。上記浸炭部材は、好ましくは、CVTシーブであるとよい(請求項3)
。より好ましくは、金属ベルトとの摺動面を有するCVTシーブであるとよい。CVTシーブは、低コスト化の要請が大きい上、摺動面に対して高い耐摩耗性が要求される部材である。そのため、この場合には、大幅なコストアップを伴うことなく摺動面の耐摩耗性を向上させることができ、本発明の効果を十分に発揮することができる。
Next, the carburized member has a sliding surface that slides with other members. Examples of this type of carburized member include CVT sheaves, outer / inner races, gears, and the like. Preferably, the carburized member is a CVT sheave (claim 3).
. More preferably, it is a CVT sheave having a sliding surface with a metal belt. The CVT sheave is a member that is highly demanded for cost reduction and that requires high wear resistance on the sliding surface. Therefore, in this case, the wear resistance of the sliding surface can be improved without significantly increasing the cost, and the effects of the present invention can be sufficiently exhibited.
また、上記浸炭部材は、その摺動面に浸炭異常層がない。浸炭異常層は、浸炭処理後の焼入れ処理時に導入されうる層であり、耐摩耗性を低下させる層である。上記浸炭部材は、最適な浸炭条件が選択されることによって浸炭異常層がなくてもよいし、焼入れ処理時に浸炭異常層が発生した場合であってもその後に仕上げ加工を実施し、これにより浸炭異常層が除去されて浸炭異常層がない状態とされていてもよい。好ましくは、後者である。浸炭異常層が確実に除去され、耐摩耗性向上の効果が大きく、信頼性も高まるからである。 Further, the carburized member does not have a carburized abnormal layer on its sliding surface. The carburizing abnormal layer is a layer that can be introduced during the quenching process after the carburizing process, and is a layer that reduces the wear resistance. The carburized member may not have an abnormal carburization layer by selecting the optimum carburizing conditions, and even if an abnormal carburization layer occurs during the quenching process, a finishing process is performed thereafter, thereby carburizing the carburizing member. The abnormal layer may be removed so that there is no carburized abnormal layer. The latter is preferred. This is because the carburized abnormal layer is surely removed, the effect of improving the wear resistance is great, and the reliability is also increased.
製造工程として焼入工程後に仕上げ加工を含む場合、仕上げ加工としては、例えば、切削、研磨などを例示することができる。これらは1または2以上組み合わせて実施することができる。上記仕上げ加工は、焼入れ処理後の摺動面を50μm〜300μmの範囲で除去する加工であることが好ましい。仕上げ加工量が50μm以上である場合には、浸炭異常層が生じている場合にこれを十分に取り除くことが可能であり、一方、300μm以下である場合には、浸炭処理により得られた硬化層を除去しすぎて表面硬さを低下させるおそれも少なくなるからである。なお、このような仕上げ加工が施される場合、上記摺動面は、切削および/または研磨の仕上げ加工後の表面ということになる。 When a finishing process is included after the quenching process as the manufacturing process, examples of the finishing process include cutting and polishing. These can be carried out by one or a combination of two or more. The finishing process is preferably a process for removing the sliding surface after quenching in the range of 50 μm to 300 μm. When the finishing amount is 50 μm or more, it is possible to sufficiently remove the carburized abnormal layer, and when it is 300 μm or less, the hardened layer obtained by carburizing treatment is obtained. This is because there is less possibility that the surface hardness will be reduced by removing too much. When such a finishing process is performed, the sliding surface is a surface after the finishing process of cutting and / or polishing.
また、上記浸炭部材は、表面炭素濃度が0.7〜0.9質量%の範囲内にある。表面炭素濃度が0.7質量%未満になると、摺動面におけるトルースタイトの発生を抑制することが難しくなる。一方、表面炭素濃度が0.9質量%を超えると、上記Cr含有量では、粒界に炭化物が析出し、強度の低下を招きやすくなる。なお、上記表面炭素濃度は、EPMAにより測定することができる。 The carburized member has a surface carbon concentration in the range of 0.7 to 0.9 mass%. When the surface carbon concentration is less than 0.7% by mass, it is difficult to suppress the occurrence of troostite on the sliding surface. On the other hand, when the surface carbon concentration exceeds 0.9% by mass, carbides are precipitated at the grain boundaries with the Cr content, and the strength tends to decrease. The surface carbon concentration can be measured by EPMA.
また、上記浸炭部材は、上記摺動面の最表面からの深さ50μmまでにおける組織のトルースタイト面積率が1%以下である。トルースタイトの面積率が1%を超える場合には、十分な耐摩耗性向上の効果が得られない。なお、上記トルースタイトの面積率は、上記摺動面の最表面からの深さ50μmまでの断面を観察し、画像解析することにより算出することができる。 The carburized member has a troostite area ratio of 1% or less in the structure up to a depth of 50 μm from the outermost surface of the sliding surface. When the area ratio of troostite exceeds 1%, a sufficient effect of improving wear resistance cannot be obtained. The area ratio of the troostite can be calculated by observing a cross section up to a depth of 50 μm from the outermost surface of the sliding surface and analyzing the image.
次に、上記浸炭部材の製造方法は、鋼部材に炭素を侵入させる浸炭期と上記鋼部材に侵入した炭素を拡散させる拡散期とを備えた浸炭処理工程と、該浸炭処理工程を経た鋼部材を焼入れする焼入工程とを有している。浸炭処理に供する鋼部材は、例えば、鍛造(熱間鍛造、冷間鍛造)や機械加工等によって、上述した化学成分を有する鋼材を所望形状に整形したものなどを好適に用いることができる。例えば、焼入れ処理後に仕上げ加工を行う場合には、上記鋼部材として上述した化学成分を有する鋼材を予め粗形状に粗加工したものなどを好適に用いることができる。 Next, the method for manufacturing the carburized member includes a carburizing period in which carbon enters the steel member and a diffusion period in which carbon invading the steel member is diffused, and a steel member that has undergone the carburizing process. A quenching process for quenching. As the steel member to be subjected to the carburizing treatment, for example, a steel material having the above-described chemical components shaped into a desired shape by forging (hot forging, cold forging), machining, or the like can be suitably used. For example, when finishing is performed after quenching, a steel material having the above-described chemical components as the steel member previously rough-processed into a rough shape can be preferably used.
ここで、上記浸炭部材の製造方法では、浸炭処理時の浸炭期におけるカーボンポテンシャル(以下、「CP」ということがある。)が1.3%以上とされる。浸炭期のCPが1.3%未満になると、摺動面等における浸炭表層にトルースタイトが発生しやすくなり、耐摩耗性が低下しやすくなる。一方、浸炭期のCPの上限は、特に限定されるものではないが、浸炭期のCPが過度に高くなると、拡散期において、所望の表面炭素濃度まで下げることが困難となったり、炭化物の粒界析出を招きやすくなる。よって、浸炭期のCPの上限は、好ましくは、2.0%であるとよい。 Here, in the manufacturing method of the carburized member, the carbon potential (hereinafter, also referred to as “CP”) in the carburizing period during the carburizing process is set to 1.3% or more. When the CP in the carburizing period is less than 1.3%, troostite is likely to be generated on the carburized surface layer on the sliding surface or the like, and the wear resistance is likely to be reduced. On the other hand, the upper limit of the CP of the carburizing period is not particularly limited, but if the CP of the carburizing period becomes excessively high, it becomes difficult to lower the surface carbon concentration to a desired level during the diffusion period, It becomes easy to invite boundary precipitation. Therefore, the upper limit of CP during the carburizing period is preferably 2.0%.
また、上記浸炭部材の製造方法では、浸炭処理時の拡散期におけるカーボンポテンシャルが0.8%以上とされることが好ましい。拡散期のCPが0.8%以上であると、浸炭部材の摺動面等における表面炭素濃度を0.7〜0.9質量%の範囲内に収めやすくなる。一方、拡散期のCPの上限は、特に限定されるものではないが、拡散期のCPが過度に高くなると、粒界炭化物の析出により部材強度が損なわれやすくなる。よって、拡散期のCPの上限は、好ましくは、0.90%であるとよい。 In the carburized member manufacturing method, the carbon potential in the diffusion period during the carburizing process is preferably 0.8% or more. When the CP in the diffusion period is 0.8% or more, the surface carbon concentration on the sliding surface or the like of the carburized member is easily contained within the range of 0.7 to 0.9% by mass. On the other hand, the upper limit of the CP during the diffusion period is not particularly limited, but if the CP during the diffusion period becomes excessively high, the strength of the member tends to be impaired due to precipitation of grain boundary carbides. Therefore, the upper limit of CP in the diffusion period is preferably 0.90%.
なお、上記浸炭処理工程における他の条件としては、例えば、ガス浸炭処理や真空浸炭処理にて浸炭処理温度900℃〜1000℃、浸炭期の時間1h〜4h、拡散期の時間1h〜4hなどを例示することができる。 As other conditions in the carburizing process, for example, a carburizing temperature of 900 ° C. to 1000 ° C., a carburizing period of 1 h to 4 h, a diffusion period of 1 h to 4 h in gas carburizing or vacuum carburizing, etc. It can be illustrated.
また、上記浸炭処理工程の後は、必要に応じて、例えば、800℃から900℃に保持した後、油焼入れ、ガス冷却等の各種の焼入れを行うことができる。さらに、上記焼入れ後、必要に応じて、焼もどし処理などを行うこともできる。焼もどし処理の条件としては、例えば、温度130℃から160℃、保持時間1h〜1.5hなどを例示することができる。さらに、上記焼入れまたは焼もどし後、必要に応じて、例えば、切削、研磨等の仕上げ加工を行うことができる。 In addition, after the carburizing treatment step, for example, after holding at 800 ° C. to 900 ° C., various quenching such as oil quenching and gas cooling can be performed. Furthermore, after the above quenching, a tempering treatment or the like can be performed as necessary. Examples of conditions for the tempering treatment include a temperature of 130 ° C. to 160 ° C. and a holding time of 1 h to 1.5 h. Furthermore, after the quenching or tempering, finishing processing such as cutting and polishing can be performed as necessary.
また、上記浸炭部材の製造方法において、上記鋼部材は摺動面を有しており、最終工程後の上記摺動面は、表面炭素濃度が0.7〜0.9質量%の範囲内にあり、最表面からの深さ50μmまでにおける組織のトルースタイト面積率が1%以下であることが好ましい(請求項8)。 In the method for manufacturing the carburized member, the steel member has a sliding surface, and the sliding surface after the final step has a surface carbon concentration within a range of 0.7 to 0.9 mass%. In addition, the troostite area ratio of the structure up to a depth of 50 μm from the outermost surface is preferably 1% or less (claim 8).
この場合には、耐摩耗性に優れた摺動面を有する浸炭部材が得られる。なお、上記最終工程としては、上記焼入れ工程、上記焼きもどし工程、上記仕上げ工程などを例示することができる。 In this case, a carburized member having a sliding surface with excellent wear resistance can be obtained. Examples of the final process include the quenching process, the tempering process, and the finishing process.
以下、実施例に係る浸炭部材、浸炭部材用鋼および浸炭部材の製造方法について説明する。 Hereinafter, the manufacturing method of the carburized member which concerns on an Example, the steel for carburized members, and the carburized member is demonstrated.
本例では、浸炭部材としてベルト式CVTのシーブを想定した。すなわち、図1に示すように、ベルト式CVT1は、入力プーリー201と出力プーリー202と、入力プーリー201および出力プーリー202に巻き掛けられた金属製のベルト3とを備える。入力プーリー201および出力プーリー202は、それぞれ円錐状の摺動面21を備えたシーブ2を2つ組み合わせて構成されている。シーブ2の摺動面21は、スチールバンド32に係合させた多数のエレメント31によって構成された金属ベルト3と常に摺動する状態で使用される。金属ベルト3に付与される張力は高く、金属製のエレメント31と接触する摺動面21は非常に高い面圧を繰り返し受けながら摩耗しやすい状態で使用される。そのため、シーブ2の摺動面21には高い耐摩耗性が要求される。
In this example, a belt type CVT sheave was assumed as the carburized member. That is, as shown in FIG. 1, the belt-
(素材鋼の準備)
素材鋼として、表1に示す化学成分を有する各種の鋼を作製した。
(Preparation of material steel)
Various steels having chemical components shown in Table 1 were produced as the raw material steel.
次に、各素材鋼から各浸炭前試験片を作製するとともに、各浸炭前試験片に対して浸炭期のCPを異ならせた浸炭処理、焼入れ、仕上げ加工を行い、各浸炭後試験片を作製した。 Next, each carburized test piece is made from each material steel, and carburized, quenched, and finished with different carburizing CPs for each pre-carburized test piece, and each post-carburized test piece is made. did.
(浸炭前試験片の作製)
各素材鋼は、30kg溶解炉にて溶解し、その鋼塊を1200℃で鍛伸した。次いで、得られた各鍛伸品に対して900℃で1時間保持した後、炉冷するという条件の焼なまし処理を行った。次いで、得られた各焼きなまし品を切削加工し、外径26.4mmの円柱状の各浸炭前試験片を作製した。
(Preparation of test specimen before carburization)
Each material steel was melted in a 30 kg melting furnace, and the steel ingot was forged at 1200 ° C. Next, each forged product obtained was annealed under the condition of holding it at 900 ° C. for 1 hour and then cooling it in the furnace. Next, each of the obtained annealed products was cut to prepare each cylindrical pre-carburization test piece having an outer diameter of 26.4 mm.
(浸炭処理、焼入れ、焼もどし、仕上げ加工)
各浸炭前試験片に対して浸炭処理、焼入れ、焼もどし、仕上げ加工を行った。具体的には、先ず、各浸炭前試験片を加熱昇温し、950℃の温度で6時間保持するガス浸炭処理を行った。この際、上記浸炭処理は、浸炭期のCPを後述する表2の通りとし、浸炭期の時間は3時間とした。また、拡散期のCPを後述する表2の通りとし、拡散期の時間は3時間とした。
(Carburizing, quenching, tempering, finishing)
Each pre-carburized specimen was carburized, quenched, tempered, and finished. Specifically, first, each carburized test piece was heated and heated, and gas carburizing treatment was performed at a temperature of 950 ° C. for 6 hours. At this time, in the carburizing process, the CP of the carburizing period was as shown in Table 2 described later, and the time of the carburizing period was 3 hours. The diffusion period CP was as shown in Table 2 described later, and the diffusion period time was 3 hours.
次いで、上記浸炭処理後、850℃まで温度を下げて1時間保持し、130℃で油焼入れを行った。次いで、上記油焼入れ後、160℃の温度に1時間保持する焼もどしを行った。次いで、上記焼もどし後、削り代200μmの切削および研磨仕上げ加工を表面に施し、浸炭異常層を除去した。以上により、外径26.0mmの円柱状の各浸炭後試験片を作製した。 Next, after the carburizing treatment, the temperature was lowered to 850 ° C. and held for 1 hour, and oil quenching was performed at 130 ° C. Next, after the oil quenching, tempering was performed at a temperature of 160 ° C. for 1 hour. Next, after the tempering, cutting and polishing finishing with a machining allowance of 200 μm were applied to the surface to remove the carburized abnormal layer. As described above, columnar post-carburized test pieces having an outer diameter of 26.0 mm were produced.
次に、その後、得られた各浸炭後試験片に対して、表面炭素濃度、トルースタイト面積率、摩耗量を測定し、評価を行った。 Next, the surface carbon concentration, the troostite area ratio, and the wear amount were measured and evaluated for each of the obtained carburized test pieces.
(表面炭素濃度)
各浸炭後試験片の表面炭素濃度をEPMAにより測定した。
(Surface carbon concentration)
The surface carbon concentration of each specimen after carburization was measured by EPMA.
(トルースタイトの面積率)
各浸炭後試験片の表面(仕上げ加工後の表面)から深さ50μmまでの断面を観察し、画像解析ソフトを用いて、トルースタイトの面積率を測定した。
(Area ratio of troostite)
A cross section from the surface of each test piece after carburization (surface after finishing) to a depth of 50 μm was observed, and the area ratio of troostite was measured using image analysis software.
(摩耗試験)
摩耗試験は、図2に示すように、浸炭後試験片5と外径φ130mmの相手方ローラ6とを用い、2ローラ接触試験により行った。この試験は、浸炭後試験片5と相手方ローラ6との周速度を異なる速度とし、滑り接触・負荷を与え、摺動面を摩耗させる試験である。試験条件は、浸炭後試験片5の回転する2000rpm、接触面圧1250MPa、滑り率−5%、潤滑油はCVTフルードという条件とした。本試験の評価は、摺動面の摩耗量によって行い、摩耗量が10μm以下の場合を耐摩耗性に優れると判断した。
以下、表2に浸炭処理条件とともに各種試験結果を示す。
(Abrasion test)
As shown in FIG. 2, the abrasion test was performed by a two-roller contact test using a
Table 2 below shows various test results together with the carburizing conditions.
表2より以下のことがわかる。すなわち、比較例は、浸炭に供した素材鋼の化学成分が本発明の規定範囲外であるか、化学成分が本発明の規定範囲内であっても浸炭処理時の浸炭期におけるCPが1.3%未満である。そのため、浸炭後試験片の表面炭素濃度が0.7質量%未満であるか、トルースタイトの面積率が1%を超えており、摩耗量が多く、耐摩耗性に劣ることがわかる。 Table 2 shows the following. That is, in the comparative example, the CP in the carburizing period at the time of carburizing treatment is 1. even if the chemical composition of the material steel subjected to carburizing is outside the specified range of the present invention or the chemical component is within the specified range of the present invention. Less than 3%. Therefore, it can be seen that the surface carbon concentration of the test piece after carburization is less than 0.7% by mass, or the area ratio of troostite exceeds 1%, the wear amount is large, and the wear resistance is inferior.
これに対して、実施例は、浸炭に供した素材鋼の化学成分が本発明の規定範囲内であり、浸炭処理時の浸炭期におけるCPが1.3%以上である。そのため、浸炭後試験片の表面炭素濃度が0.7質量%〜0.9質量%の範囲内であり、トルースタイトの面積率が1%以下であり、摩耗量が少なく、耐摩耗性に優れていることがわかる。 On the other hand, in the examples, the chemical composition of the material steel subjected to carburization is within the specified range of the present invention, and the CP in the carburizing period during the carburizing process is 1.3% or more. Therefore, the surface carbon concentration of the test piece after carburization is in the range of 0.7 mass% to 0.9 mass%, the area ratio of troostite is 1% or less, the wear amount is small, and the wear resistance is excellent. You can see that
上記から、本発明によれば、大幅なコストアップを伴うことなく摺動面等の耐摩耗性に優れた浸炭部材、これの半製品である浸炭部材用鋼、浸炭部材の製造方法を提供できることがわかる。 From the above, according to the present invention, it is possible to provide a carburized member excellent in wear resistance such as a sliding surface without significant cost increase, a steel for carburized member which is a semi-finished product thereof, and a method for manufacturing the carburized member. I understand.
以上、実施例について説明したが、本発明は、上記実施例により限定されるものではなく、本発明の趣旨を逸脱しない範囲内で種々の改変を行うことが可能である。 Although the embodiments have been described above, the present invention is not limited to the above embodiments, and various modifications can be made without departing from the spirit of the present invention.
1 ベルト式無段変速機(ベルト式CVT)
2 CVTシーブ
21 摺動面
201 入力プーリー
202 出力プーリー
3 ベルト
31 エレメント
32 スチールバンド
1 Belt type continuously variable transmission (Belt type CVT)
2
Claims (8)
化学成分が、質量%で、C:0.10〜0.30%、Si:0.50〜2.00%、Mn:0.30〜1.50%、P:0.035%以下、S:0.035%以下、Cr:1.35〜3.00%、Al:0.020〜0.060%、および、N:0.0080〜0.0250%を含有し、残部がFeおよび不可避不純物よりなり、
上記摺動面は、浸炭異常層がなく、表面炭素濃度が0.7〜0.9質量%の範囲内にあり、最表面からの深さ50μmまでにおける組織のトルースタイト面積率が1%以下であることを特徴とする浸炭部材。 A carburized member having a sliding surface,
Chemical component is mass%, C: 0.10 to 0.30%, Si: 0.50 to 2.00%, Mn: 0.30 to 1.50%, P: 0.035% or less, S : 0.035% or less, Cr: 1.35 to 3.00%, Al: 0.020 to 0.060%, and N: 0.0080 to 0.0250%, the balance being Fe and inevitable Consisting of impurities,
The sliding surface has no carburized abnormal layer, the surface carbon concentration is in the range of 0.7 to 0.9 mass%, and the troostite area ratio of the structure at a depth of 50 μm from the outermost surface is 1% or less. A carburized member characterized by being.
上記化学成分が、さらにMo:0.80%以下を含有することを特徴とする浸炭部材。 The carburized member according to claim 1,
The carburized member, wherein the chemical component further contains Mo: 0.80% or less.
化学成分が、質量%で、C:0.10〜0.30%、Si:0.50〜2.00%、Mn:0.30〜1.50%、P:0.035%以下、S:0.035%以下、Cr:1.35〜3.00%、Al:0.020〜0.060%、および、N:0.0080〜0.0250%を含有し、残部がFeおよび不可避不純物よりなることを特徴とする浸炭部材用鋼。 The sliding surface has no abnormal carburization layer, has a surface carbon concentration within a range of 0.7 to 0.9 mass%, and has a structure with a depth of 50 μm from the outermost surface. It is a steel for carburizing member used for manufacturing a carburized member having a tight area ratio of 1% or less,
Chemical component is mass%, C: 0.10 to 0.30%, Si: 0.50 to 2.00%, Mn: 0.30 to 1.50%, P: 0.035% or less, S : 0.035% or less, Cr: 1.35 to 3.00%, Al: 0.020 to 0.060%, and N: 0.0080 to 0.0250%, the balance being Fe and inevitable A steel for carburized members, characterized by comprising impurities.
上記化学成分が、さらにMo:0.80%以下を含有することを特徴とする浸炭部材。 In the carburized member steel according to claim 4,
The carburized member, wherein the chemical component further contains Mo: 0.80% or less.
上記鋼部材は、化学成分が、質量%で、C:0.10〜0.30%、Si:0.50〜2.00%、Mn:0.30〜1.50%、P:0.035%以下、S:0.035%以下、Cr:1.35〜3.00%、Al:0.020〜0.060%、および、N:0.0080〜0.0250%を含有し、残部がFeおよび不可避不純物よりなり、
上記浸炭期におけるカーボンポテンシャルは1.3%以上とされることを特徴とする浸炭部材の製造方法。 A carburized member having a carburizing process in which carbon enters the steel member and a diffusion period in which carbon that has entered the steel member is diffused, and a quenching process in which the steel member that has undergone the carburizing process is quenched. A manufacturing method of
The steel member has a chemical composition of mass%, C: 0.10 to 0.30%, Si: 0.50 to 2.00%, Mn: 0.30 to 1.50%, P: 0.00. 035% or less, S: 0.035% or less, Cr: 1.35 to 3.00%, Al: 0.020 to 0.060%, and N: 0.0080 to 0.0250%, The balance consists of Fe and inevitable impurities,
A method for producing a carburized member, wherein a carbon potential in the carburizing period is 1.3% or more.
上記化学成分が、さらにMo:0.80%以下を含有することを特徴とする浸炭部材の製造方法。 In the manufacturing method of the carburized member of Claim 6,
The said chemical component contains Mo: 0.80% or less further, The manufacturing method of the carburized member characterized by the above-mentioned.
上記鋼部材は摺動面を有しており、最終工程後の上記摺動面は、表面炭素濃度が0.7〜0.9質量%の範囲内にあり、最表面からの深さ50μmまでにおける組織のトルースタイト面積率が1%以下であることを特徴とする浸炭部材の製造方法。 In the manufacturing method of the carburized member according to claim 6 or 7,
The steel member has a sliding surface, and the sliding surface after the final process has a surface carbon concentration in the range of 0.7 to 0.9 mass%, and a depth from the outermost surface to 50 μm. A method for producing a carburized member, wherein the troostite area ratio of the structure is 1% or less.
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