JP2817364B2 - Heat resistant high toughness steel - Google Patents
Heat resistant high toughness steelInfo
- Publication number
- JP2817364B2 JP2817364B2 JP16921690A JP16921690A JP2817364B2 JP 2817364 B2 JP2817364 B2 JP 2817364B2 JP 16921690 A JP16921690 A JP 16921690A JP 16921690 A JP16921690 A JP 16921690A JP 2817364 B2 JP2817364 B2 JP 2817364B2
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- temperature
- toughness
- steel
- quenching
- weight
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Description
【発明の詳細な説明】 「産業上の利用分野」 本発明は、耐熱高靭性鋼に係り、特に、高強度域での
靭性を向上させたものである。DETAILED DESCRIPTION OF THE INVENTION "Industrial application field" The present invention relates to a heat-resistant and high-toughness steel, and more particularly, to an improvement in toughness in a high-strength region.
「従来の技術」 従来、高温環境で高強度及び高靭性が要求される歯
車、燃料噴射弁、切削工具等の用途に鋼材を適合させる
方法として、浸炭焼入れ法があるが、形状的な制限を受
け易く硬度は高くなるものの、高温雰囲気での靭性が十
分なものとはなりにくい等の課題がある。"Conventional technology" Conventionally, there is a carburizing and quenching method as a method of adapting steel to applications such as gears, fuel injection valves, and cutting tools that require high strength and high toughness in a high-temperature environment. Although it is easy to receive and has high hardness, there are problems such as that it is difficult to obtain sufficient toughness in a high-temperature atmosphere.
そこで、高温環境にさらされる部分に、送油ポンプ等
によって冷却油を送り込んで冷却することが一般に行な
われている。Therefore, cooling is generally performed by sending cooling oil to a portion exposed to a high-temperature environment by an oil feed pump or the like.
一方、一部の工具鋼、例えばJIS規格(日本工業規
格)準拠のSKH−51鋼にあっては、高温環境でかつ高強
度(高硬度)域においても比較的高靭性が得られるもの
とされている。On the other hand, some tool steels, such as SKH-51 steel conforming to JIS (Japanese Industrial Standards), are said to have relatively high toughness even in high temperature environments and high strength (high hardness) regions. ing.
「発明が解決しようとする課題」 しかし、冷却油によって発熱箇所を冷却する方法であ
ると、摩擦熱等の仕事熱を発生する部分を冷却するため
の送油ポンプや冷却装置等が必要であり、発熱鋼材の耐
熱性が低い場合には、多量の冷却油を供給循環させるた
めに、冷却装置を大型化する必要が生じて経済性が損な
われてしまうことになる。[Problems to be Solved by the Invention] However, in the method of cooling a heat-generating portion with cooling oil, an oil feed pump or a cooling device for cooling a portion that generates work heat such as frictional heat is required. On the other hand, when the heat resistance of the heat-generating steel material is low, a large amount of cooling oil is supplied and circulated, so that it is necessary to increase the size of the cooling device, which impairs economic efficiency.
そして、前記SKH−51鋼であると、高温状態で所望の
硬さと靭性とを同時に満足させることが困難である。When the SKH-51 steel is used, it is difficult to simultaneously satisfy desired hardness and toughness in a high temperature state.
本発明は、上記事情に鑑みてなされたもので、高温及
び高強度域で比較的高い靭性をることを目的とするもの
である。The present invention has been made in view of the above circumstances, and has as its object to provide relatively high toughness in a high temperature and high strength region.
「課題を解決するための手段」 かかる課題を解決する2つの手段を提案している。"Means for Solving the Problem" There are proposed two means for solving the problem.
第1の手段は、下記組成を有する合金材を焼入れ及び
高温焼戻し処理してなる耐熱高靭性鋼としている。The first means is a heat-resistant high-toughness steel obtained by quenching and high-temperature tempering an alloy material having the following composition.
C :0.5〜0.6重量% Si:0.4 重量%以下 Mn:0.3〜0.5重量% Cr:3.5〜4.5重量% Mo:4.5〜5.5重量% W :5.0〜7.0重量% V :0.7〜0.9重量% Fe:残部 第2の手段は、熱処理条件が、焼入れ温度1150±50
℃、焼戻し温度530±30℃である構成を第1の手段に付
加してなる耐熱高靭性鋼としている。C: 0.5 to 0.6% by weight Si: 0.4% by weight or less Mn: 0.3 to 0.5% by weight Cr: 3.5 to 4.5% by weight Mo: 4.5 to 5.5% by weight W: 5.0 to 7.0% by weight V: 0.7 to 0.9% by weight Fe: The second means is that the heat treatment condition is a quenching temperature of 1150 ± 50.
° C and a tempering temperature of 530 ± 30 ° C are added to the first means to form a heat-resistant and high-toughness steel.
「作用」 第1及び第2の手段に係る耐熱高靭性鋼にあっては、
ヴィッカースかたさがHv650〜760の範囲内で、靭性が顕
著に向上する傾向が現れる。また、焼入れ温度が1100〜
1200℃の範囲であると、ち密な組織を維持する。"Action" In the heat-resistant and high-toughness steel according to the first and second means,
When the Vickers hardness is in the range of Hv 650 to 760, a tendency to significantly improve toughness appears. Also, the quenching temperature is 1100 ~
When the temperature is in the range of 1200 ° C., a dense tissue is maintained.
「実施例」 第1表に示す組成を有する合金材を、焼入れ及び高温
焼戻し処理して、目的とする耐熱高靭性鋼を作成した。Example An alloy material having the composition shown in Table 1 was subjected to quenching and high-temperature tempering to produce a target heat-resistant and high-toughness steel.
この場合の熱処理条件は、焼入れ温度が1150±50℃の
範囲、焼戻し温度が530±30℃の範囲内に設定し、これ
らの組み合わせによって硬さを調整したものを作成し
た。 The heat treatment conditions in this case were set such that the quenching temperature was in the range of 1150 ± 50 ° C. and the tempering temperature was in the range of 530 ± 30 ° C., and the hardness was adjusted by a combination of these.
<硬さと靭性の関係> 得られた耐熱高靭性鋼(実施例サンプル)について、
硬さと靭性との関係を求めた。その結果を第1図に示
す。比較のため、JIS規格の工具鋼に準拠する高速度鋼
(SKH−51材・比較サンプル)の特性を併記した。<Relationship between hardness and toughness> Regarding the obtained heat-resistant and high-toughness steel (example sample),
The relationship between hardness and toughness was determined. The result is shown in FIG. For comparison, the characteristics of a high-speed steel (SKH-51 material, comparative sample) based on JIS standard tool steel are also shown.
第1図における実施例サンプルの曲線Aと、比較サン
プルの曲線Bとの比較から明らかなように、曲線Aで
は、ヴィッカースかたさがHv650〜760の範囲内で、靭性
が顕著に向上する傾向を示しており、曲線Bの比較サン
プルと比較して、実施例サンプルの優位性が明らかであ
る。As is clear from the comparison between the curve A of the example sample in FIG. 1 and the curve B of the comparative sample, the curve A shows a tendency that the toughness is significantly improved when the Vickers hardness is in the range of Hv650 to 760. As compared with the comparative sample of the curve B, the superiority of the example sample is apparent.
<焼入れ温度と組織の関係> 実施例サンプル及び比較サンプルにおいて、その焼入
れ処理条件を、4段階の温度1100℃、1150℃、1200℃、
1250度、30分、油冷とし、焼戻し処理条件を525℃、120
分、空冷とする熱処理を行なった後、5%ピラクル液に
よって腐食させた場合の組織の顕微鏡写真を第2図なし
い第5図に示す。これら各図において、(A)は実施例
サンプル、(B)は比較サンプルである。ただし、 第2図(A)(B)は焼入れ温度1100℃、 第3図(A)(B)は焼入れ温度1150℃、 第4図(A)(B)は焼入れ温度1200℃、 第5図(A)(B)は焼入れ温度1250℃である。<Relationship between quenching temperature and structure> In the example sample and the comparative sample, the quenching treatment conditions were set to four stages of temperatures of 1100 ° C, 1150 ° C, 1200 ° C,
1250 degrees, 30 minutes, oil-cooled, tempering treatment conditions 525 ℃, 120
FIG. 2 to FIG. 5 show micrographs of the structure in the case where the microstructure was corroded by 5% Pilacle solution after the heat treatment for air cooling. In each of these figures, (A) is an example sample and (B) is a comparative sample. However, FIGS. 2 (A) and (B) show a quenching temperature of 1100 ° C., FIGS. 3 (A) and (B) show a quenching temperature of 1150 ° C., FIGS. 4 (A) and (B) show a quenching temperature of 1200 ° C. (A) and (B) show a quenching temperature of 1250 ° C.
第2図ないし第5図において、(A)(B)を比較す
ると、実施例サンプルは、焼入れ温度1100〜1200℃の範
囲で、緻密な組織を維持するのに対し、比較サンプル
は、1150〜1200℃で組織が粗くなる傾向を示した。そし
て、焼入れ温度が1250℃である場合は、比較サンプルで
は粒界に炭化物が析出して脆くなる傾向が現れ、実施例
サンプルでは、粒界割れが生じる傾向が現れた。2 to 5, comparing (A) and (B), the sample of the example maintains a dense structure at a quenching temperature of 1100 to 1200 ° C., whereas the sample of the comparative example has a quenching temperature of 1150 to 1200 ° C. At 1200 ° C, the structure tended to become coarse. When the quenching temperature was 1250 ° C., carbides tended to precipitate at the grain boundaries in the comparative sample, and became brittle, and in the example samples, grain boundary cracks appeared.
したがって、実施例サンプルでは、ヴィッカースかた
さがHv650〜760の範囲内である場合に有用性が高く、焼
入れ温度が1100〜1200℃以下であると、ち密な組織を維
持するものとの結論が得られる。Therefore, in the example sample, the usefulness is high when the Vickers hardness is in the range of Hv650 to 760, and when the quenching temperature is 1100 to 1200 ° C or less, it can be concluded that the dense structure is maintained. .
<雰囲気温度と硬さの関係> 第6図は、実施例サンプル及び比較サンプルにおける
温度−硬さの低下の特性を示すものであり、マイクロビ
ッカース硬度計を使用して、雰囲気温度20℃ないし400
℃での硬さ(MHV500)の低下を計測したものである。第
6図に示すように、室温20℃における硬さを基準(0)
とした場合、高温となるにしたがって硬さが低下する傾
向を示すが、実施例サンプル(A)にあっては、焼戻し
温度付近まで、実用上十分な硬度を維持することが確認
された。また、比較サンプル(B)にあっては、硬度の
低下が相対的に大きくなる傾向が認められる。<Relationship Between Ambient Temperature and Hardness> FIG. 6 shows the temperature-hardness reduction characteristics of the example sample and the comparative sample.
It is a measure of the decrease in hardness (MHV500) at ° C. As shown in FIG. 6, the hardness at room temperature of 20 ° C. is standard (0).
In this case, the hardness tends to decrease as the temperature increases, but it was confirmed that practically sufficient hardness was maintained in the example sample (A) up to near the tempering temperature. Moreover, in the comparative sample (B), a tendency that the decrease in hardness is relatively large is recognized.
「発明の効果」 以上説明したように、本発明における耐熱高靭性鋼
は、中炭素−4%クロム−5%モリブデン−6%タング
ステン−0.8%組成とし、かつ、適正な焼入れ及び焼戻
し処理を行なうことにより、硬度がHv650〜760の範囲内
である場合に、靭性が従来例の工具鋼と比較して高くな
り、高温雰囲気での温度、靭性を保持することができ
る。[Effects of the Invention] As described above, the heat-resistant and high-toughness steel according to the present invention has a composition of medium carbon-4% chromium-5% molybdenum-6% tungsten-0.8%, and performs appropriate quenching and tempering. Thereby, when the hardness is in the range of Hv650 to 760, the toughness is higher than that of the conventional tool steel, and the temperature and toughness in a high-temperature atmosphere can be maintained.
上記により、摩擦及び摺動面を有して高温化し易い機
器等に適し、優れた高温特性と相まって浸炭素面硬化処
理が不適当な部品への応用性が高まるとともに、従来例
と比較して冷却装置の簡素化を図ることができる等の優
れた効果を奏するものである。As described above, it is suitable for equipment that has a friction and sliding surface and is easily heated to high temperature. This provides excellent effects such as simplification of the device.
第1図は本発明に係る耐熱高靭性鋼及び比較のために高
速度鋼の特性を併記した硬さと靭性との関係曲線図であ
る。 第2図(A)は焼入れ温度1100℃で処理した実施例サン
プルの鋼材を腐食させた場合の金属組織の顕微鏡写真を
示すものである。 第2図(B)は焼入れ温度1100℃で処理した比較サンプ
ルの鋼材を腐食させた場合の金属組織の顕微鏡写真を示
すものである。 第3図(A)は焼入れ温度1150℃で処理した実施例サン
プルの鋼材を腐食させた場合の金属組織の顕微鏡写真を
示すものである。 第3図(B)は焼入れ温度1150℃で処理した比較サンプ
ルの鋼材を腐食させた場合の金属組織の顕微鏡写真を示
すものである。 第4図(A)は焼入れ温度1200℃で処理した実施例サン
プルの鋼材を腐食させた場合の金属組織の顕微鏡写真を
示すものである。 第4図(B)は焼入れ温度1200℃で処理した比較サンプ
ルの鋼材を腐食させた場合の金属組織の顕微鏡写真を示
すものである。 第5図(A)は焼入れ温度1250℃で処理した実施例サン
プルの鋼材を腐食させた場合の金属組織の顕微鏡写真を
示すものである。 第5図(B)は焼入れ温度1250℃で処理した比較サンプ
ルの鋼材を腐食させた場合の金属組織の顕微鏡写真を示
すものである。 第6図は実施例サンプル及び比較サンプルにおける温度
−硬さの低下の関係を示す特性図である。FIG. 1 is a graph showing the relationship between hardness and toughness, together with characteristics of a heat-resistant high-toughness steel according to the present invention and a high-speed steel for comparison. FIG. 2 (A) is a photomicrograph of the metallographic structure when the steel material of the example sample treated at a quenching temperature of 1100 ° C. is corroded. FIG. 2 (B) shows a micrograph of the metal structure of a comparative sample treated at a quenching temperature of 1100 ° C. when the steel material is corroded. FIG. 3 (A) is a photomicrograph of the metallographic structure when the steel material of the example sample treated at a quenching temperature of 1150 ° C. is corroded. FIG. 3 (B) is a photomicrograph of the metal structure of a comparative sample treated at a quenching temperature of 1150 ° C. when the steel is corroded. FIG. 4 (A) is a photomicrograph of the metallographic structure when the steel material of the example sample treated at a quenching temperature of 1200 ° C. was corroded. FIG. 4 (B) shows a micrograph of the metal structure of a comparative sample treated at a quenching temperature of 1200 ° C. when the steel material is corroded. FIG. 5 (A) is a photomicrograph of the metallographic structure when the steel material of the example sample treated at a quenching temperature of 1250 ° C. was corroded. FIG. 5 (B) is a photomicrograph of the metal structure of a comparative sample treated at a quenching temperature of 1250 ° C. when the steel is corroded. FIG. 6 is a characteristic diagram showing the relationship between the temperature and the decrease in hardness in the example sample and the comparative sample.
───────────────────────────────────────────────────── フロントページの続き (58)調査した分野(Int.Cl.6,DB名) C22C 38/00 - 38/60 C21D 6/00 101──────────────────────────────────────────────────続 き Continued on front page (58) Field surveyed (Int. Cl. 6 , DB name) C22C 38/00-38/60 C21D 6/00 101
Claims (2)
焼戻し処理してなることを特徴とする耐熱高靭性鋼。 C :0.5〜0.6重量% Si:0.4 重量%以下 Mn:0.3〜0.5重量% Cr:3.5〜4.5重量% Mo:4.5〜5.5重量% W :5.0〜7.0重量% V :0.7〜0.9重量% Fe:残部1. A heat-resistant and high-toughness steel obtained by quenching and high-temperature tempering an alloy material having the following composition. C: 0.5 to 0.6% by weight Si: 0.4% by weight or less Mn: 0.3 to 0.5% by weight Cr: 3.5 to 4.5% by weight Mo: 4.5 to 5.5% by weight W: 5.0 to 7.0% by weight V: 0.7 to 0.9% by weight Fe: Rest
戻し温度530±30℃であることを特徴とする請求項i記
載の耐熱高靭性鋼。2. The heat-resistant and high-toughness steel according to claim 1, wherein the heat treatment conditions are a quenching temperature of 1150 ± 50 ° C. and a tempering temperature of 530 ± 30 ° C.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP16921690A JP2817364B2 (en) | 1990-06-27 | 1990-06-27 | Heat resistant high toughness steel |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP16921690A JP2817364B2 (en) | 1990-06-27 | 1990-06-27 | Heat resistant high toughness steel |
Publications (2)
Publication Number | Publication Date |
---|---|
JPH0459945A JPH0459945A (en) | 1992-02-26 |
JP2817364B2 true JP2817364B2 (en) | 1998-10-30 |
Family
ID=15882369
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP16921690A Expired - Lifetime JP2817364B2 (en) | 1990-06-27 | 1990-06-27 | Heat resistant high toughness steel |
Country Status (1)
Country | Link |
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JP (1) | JP2817364B2 (en) |
Families Citing this family (1)
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CN115430995B (en) * | 2022-09-05 | 2024-05-24 | 攀钢集团成都钢钒有限公司 | Manufacturing method of 50Mn18Cr4V nonmagnetic steel pipe |
-
1990
- 1990-06-27 JP JP16921690A patent/JP2817364B2/en not_active Expired - Lifetime
Also Published As
Publication number | Publication date |
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JPH0459945A (en) | 1992-02-26 |
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