JP3118346B2 - Tooth wheel - Google Patents
Tooth wheelInfo
- Publication number
- JP3118346B2 JP3118346B2 JP05117862A JP11786293A JP3118346B2 JP 3118346 B2 JP3118346 B2 JP 3118346B2 JP 05117862 A JP05117862 A JP 05117862A JP 11786293 A JP11786293 A JP 11786293A JP 3118346 B2 JP3118346 B2 JP 3118346B2
- Authority
- JP
- Japan
- Prior art keywords
- weight
- less
- grain boundary
- content
- gear
- 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.)
- Expired - Lifetime
Links
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- Gears, Cams (AREA)
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
Description
【０００１】[0001]
【産業上の利用分野】本発明は衝撃特性と疲労特性に優
れた歯車に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a gear having excellent impact characteristics and fatigue characteristics.
【０００２】[0002]
【従来の技術】従来から歯車は肌焼鋼を浸炭処理した素
材により構成され、表面は耐摩耗性を有し内部は靱性を
保つようにされている。2. Description of the Related Art Conventionally, gears are made of a material obtained by carburizing case-hardened steel, the surface of which is wear-resistant, and the inside of which is maintained tough.
【０００３】[0003]
【発明が解決しようとする課題】しかしながら上記従来
の歯車は素材中に粒界酸化層が生成するので、これを起
点として亀裂が発生し易く、また靱性向上のためにいた
ずらに合金元素を添加した場合は、被削性を低下させる
と云う問題点があった。However, in the conventional gear described above, since a grain boundary oxide layer is formed in the raw material, cracks are likely to occur from this as a starting point, and alloy elements are added unnecessarily to improve toughness. In such a case, there is a problem that the machinability is reduced.
【０００４】[0004]
【課題を解決するための手段】本発明は上記従来の課題
を解決するための手段として、Ｃ０．１５〜０．２５重
量％，Ｓi ０．１重量％以下，Ｍn ０．２〜０．８重量
％，Ｐ０．０１５重量％以下，Ｓ０．０１０〜０．０１
５重量％，Ｎi ０．４〜０．６重量％，Ｃr ０．２〜
０．８重量％，Ｍo ０．６〜１．０重量％，Ａl ０．０
１〜０．０５重量％，Ｎ０．００５〜０．０２５重量
％，Ｎb ０．０２〜０．５重量％，Ｏ０．００２重量％
以下，残部はＦe であり、１０Ｓi ＋Ｍn ＋Ｃr ≦２．
０である素材であって、該素材はＣ濃度が０．７〜０．
９重量％となるよう浸炭処理されており、６μｍ以下の
浸炭異常層を有しかつ♯９以上の結晶粒度を有する素材
によって構成された歯車を提供するものである。According to the present invention, as a means for solving the above-mentioned conventional problems, C is 0.15 to 0.25% by weight, Si is 0.1% by weight or less, and Mn is 0.2 to 0.8%. % By weight, P 0.015% by weight or less, S0.010 to 0.01
5% by weight, Ni 0.4-0.6% by weight, Cr 0.2-
0.8% by weight, Mo 0.6 to 1.0% by weight, Al 0.0
1-0.05% by weight, N 0.005-0.025% by weight, Nb 0.02-0.5% by weight, O 0.002% by weight
Hereinafter, the remainder is Fe, and 10Si + Mn + Cr ≦ 2.
0, which has a C concentration of 0.7-0.
An object of the present invention is to provide a gear that has been carburized to 9% by weight, has a carburized abnormal layer of 6 μm or less, and is made of a material having a crystal grain size of # 9 or more.
【０００５】[0005]
【作用】本発明の作用は下記の通りである。Ｃは０．１
５重量％（以下単に％とする）未満の含有量では歯車心
部の強度を確保出来ず、また０．２５％を越える含有量
では歯車の靱性が低下する。Ｓi は０．１％を越える含
有量では粒界酸化層が増加し、粒界近傍の強度を低下さ
せる。従来の肌焼鋼ではＳi が０．１５〜０．３５％含
まれていたため、上記した亀裂が発生し易い。Ｍn は焼
入性を向上せしめるが、０．２％未満の含有量では焼入
性を確保出来ず、また０．８％を越える含有量では粒界
酸化層が増加する傾向がある。Ｐは０．０１５％を越え
る含有量で粒界偏折作用があり、粒界を脆化せしめる傾
向がある。ＳはＭn と同様展延性のある化合物を形成
し、横方向の衝撃値を低下させ、被削性を向上せしめる
が０．０１０％未満の含有量では被削性を確保出来ず、
また０．０１５％を越える含有量では靱性が低下する。
Ｎi は０．４％未満の含有量では粒内強度を確保出来
ず、また０．６％を越える含有量では被削性が低下す
る。Ｃr は０．２％未満の含有量では焼入性が確保出来
ず、また０．８％を越える含有量では粒界酸化層が増加
する傾向がある。Ｍo はＰの粒界偏折作用を抑制して粒
界強度を向上せしめ、また不完全焼入組織の生成を押さ
える効果があるが、０．６％未満の含有量では粒界強度
が確保出来ず、しかし１．０％を越える含有量では効果
は飽和する。Ａl は０．０１０％未満の含有量では結晶
粒の微細化が確保出来ず、また０．０５％を越える含有
量では効果が飽和する。結晶粒を微細化すれば亀裂伝播
抵抗が増すために浸炭層の靱性向上に有効である。Ｎは
Ａl と同様に結晶粒微細化効果を有するが、０．００５
％未満の含有量では上記効果は確保出来ず、０．０２５
％を越える含有量では効果は飽和する。Ｎb はＡl と同
様に結晶粒微細化効果を有するが、０．０２％未満の含
有量では上記効果は確保出来ず、０．５％を越える含有
量では効果は飽和する。Ｏは０．００２％を越える含有
量ではアルミナ介在物の生成による疲労破壊の原因とな
る。The operation of the present invention is as follows. C is 0.1
If the content is less than 5% by weight (hereinafter simply referred to as "%"), the strength of the gear core cannot be secured, and if the content exceeds 0.25%, the toughness of the gear decreases. If the content of Si exceeds 0.1%, the grain boundary oxide layer increases, and the strength near the grain boundaries decreases. Since the conventional case hardening steel contains 0.15 to 0.35% of Si, the above-described cracks are easily generated. Although Mn improves the hardenability, hardenability cannot be secured at a content of less than 0.2%, and a grain boundary oxide layer tends to increase at a content of more than 0.8%. If P is contained in an amount exceeding 0.015%, it has a grain boundary bending effect, and tends to embrittle the grain boundary. S forms a malleable compound like Mn, reduces the impact value in the lateral direction, and improves machinability. However, if the content is less than 0.010%, machinability cannot be secured.
If the content exceeds 0.015%, the toughness decreases.
If the Ni content is less than 0.4%, the intragranular strength cannot be ensured, and if the Ni content exceeds 0.6%, the machinability decreases. If the content of Cr is less than 0.2%, hardenability cannot be ensured, and if the content exceeds 0.8%, the grain boundary oxide layer tends to increase. Mo has the effect of suppressing the grain boundary bending effect of P and improving the grain boundary strength, and also has the effect of suppressing the formation of an incompletely quenched structure. However, when the content exceeds 1.0%, the effect saturates. If the content of Al is less than 0.010%, the refinement of the crystal grains cannot be secured, and if the content exceeds 0.05%, the effect is saturated. Refining the crystal grains increases the crack propagation resistance, and is effective in improving the toughness of the carburized layer. N has a crystal grain refining effect like Al, but 0.005%.
%, The above effect cannot be secured.
If the content exceeds%, the effect is saturated. Nb has a crystal grain refining effect similarly to Al, but the above effect cannot be secured if the content is less than 0.02%, and the effect is saturated if the content exceeds 0.5%. O content exceeding 0.002% causes fatigue fracture due to formation of alumina inclusions.
【０００６】浸炭異常層（粒界酸化層）を６μｍ以下と
すると歯車の衝撃強度や疲労強度が向上する。上記粒界
酸化層の深さと素材に含まれる元素との関係は１０Ｓi
＋Ｍn ＋Ｃr をパラメーターとし、粒界酸化層を６μｍ
以下とするためには上記パラメーターを２．０以下とす
る必要がある。また結晶粒度を♯９（ＪＩＳ）以上とす
ることによって結晶粒内の強度が高められる。When the thickness of the abnormal carburized layer (grain boundary oxide layer) is set to 6 μm or less, the impact strength and fatigue strength of the gear are improved. The relationship between the depth of the grain boundary oxide layer and the elements contained in the material is 10Si.
+ Mn + Cr as parameters, and the grain boundary oxide layer is 6 μm
In order to achieve the following, the above parameters need to be 2.0 or less. Further, by setting the crystal grain size to ♯9 (JIS) or more, the strength in the crystal grain is increased.
【０００７】[0007]
【実施例】表１に示す合金成分の鋼を溶製。圧延、焼な
らしした後試験片に加工した。該試験片について浸炭焼
入焼もどしを以下の条件で実施した。プロパンガスを炭
素源として使用し９１０℃にて浸炭・拡散を行ない、そ
の後８３０℃で３０分保持後油冷した。このように処理
した試験片は更に１６０℃で２時間の焼もどし後空冷し
た。EXAMPLES Steels having the alloy components shown in Table 1 were melted. After rolling and normalizing, it was processed into a test piece. Carburizing, quenching and tempering of the test piece were performed under the following conditions. Carburization and diffusion were carried out at 910 ° C. using propane gas as a carbon source, and then kept at 830 ° C. for 30 minutes and then oil-cooled. The test piece treated in this way was further tempered at 160 ° C. for 2 hours and then air-cooled.
【０００８】[0008]
【表１】 [Table 1]
【０００９】試験項目；焼ならし硬さ、粒界酸化層深
さ、オーステナイト結晶粒度、 被削性：ハイスドリル加工による５０００mm寿命速度で
評価 歯車疲れ試験：ピッチ円直径７０mm，モジュール２．
５，歯数２８の歯車で１０7 回の寿命を評価 回転曲げ疲れ試験：平行部８mmの小野式平滑試験片 浸炭衝撃試験：歯車疲れ試験と同一の歯車を用いアイゾ
ット試験 上記試験結果を表２に示す。Test items: normalizing hardness, grain boundary oxide layer depth, austenite grain size, machinability: evaluated at a life speed of 5000 mm by high speed drilling Gear fatigue test: pitch circle diameter 70 mm, module 2.
5, gears 10 7 times the lifetime bending evaluation rotation fatigue test of the number of teeth 28: Ono smooth specimen carburization impact test of the parallel portion 8 mm: Table 2 Izod Test The test results using the same gear and the gear Fatigue Test Shown in
【００１０】[0010]
【表２】 [Table 2]
【００１１】本発明鋼であるＡ，Ｂは疲れ強さ、衝撃強
さともに良好であることに加え、焼ならし後の硬さもＮ
i 未添加鋼とほぼ同等の値であるため、被削性の低下が
殆ど見られない。ＣおよびＤの比較鋼は従来の肌焼鋼で
あるがＳi が過大であるために粒界酸化が顕著に認めら
れ、特に衝撃強さが他に比べ大幅に低下している。Ｅお
よびＨの比較鋼はＮi が過大であり、衝撃値等は良好で
あるが被削性が大幅に低下している。ＦおよびＧの比較
鋼は夫々Ｎi とＭo が過少であるため、疲れ強さや衝撃
強さに低い値が認められる。The steels A and B of the present invention have good fatigue strength and impact strength, and also have a hardness after normalizing of N.
i Since the value is almost the same as that of the unadded steel, the machinability hardly decreases. Comparative steels C and D are conventional case hardened steels, but because Si is excessive, grain boundary oxidation is remarkably recognized, and particularly, impact strength is significantly reduced as compared with other steels. The comparative steels of E and H have excessive Ni, and have good impact values and the like, but their machinability is greatly reduced. Since the comparative steels of F and G have too low Ni and Mo, respectively, low values of fatigue strength and impact strength are recognized.
【００１２】粒界酸化層深さＤ（μｍ）とパラメーター
Ｘ（１０Ｓi ＋Ｍn ＋Ｃr ）との関係をグラフにすると
図１のようになり、ＤとＸとは略リニヤな関係を示し、
Ｘが２．０以下で Ｄが６μｍ以下になることが判る。A graph showing the relationship between the grain boundary oxide layer depth D (μm) and the parameter X (10Si + Mn + Cr) is as shown in FIG. 1, where D and X show a substantially linear relationship.
It can be seen that when X is 2.0 or less, D becomes 6 μm or less.
【００１３】[0013]
【発明の効果】したがって本発明においては、衝撃強度
や疲労強度に優れた歯車を得ることが出来る。Thus, in the present invention, a gear having excellent impact strength and fatigue strength can be obtained.
【図１】粒界酸化層深さＤ（μｍ）を縦軸に、パラメー
ターＸを横軸にとったグラフである。FIG. 1 is a graph in which a vertical axis represents a grain boundary oxide layer depth D (μm) and a horizontal axis represents a parameter X.
フロントページの続き (72)発明者 水野 孝樹 埼玉県和光市中央１丁目４番１号 株式 会社本田技術研究所内 (56)参考文献 特開 昭60−21359（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) C23C 8/22 Continuation of front page (72) Inventor Takaki Mizuno 1-4-1 Chuo, Wako-shi, Saitama Pref. Honda Research Institute, Ltd. (56) References JP-A-60-21359 (JP, A) (58) Fields investigated (Int.Cl. 7 , DB name) C23C 8/22
Claims (1)
重量％以下，Ｍn ０．２〜０．８重量％，Ｐ０．０１５
重量％以下，Ｓ０．０１０〜０．０１５重量％，Ｎi
０．４〜０．６重量％，Ｃr ０．２〜０．８重量％，Ｍ
o ０．６〜１．０重量％，Ａl ０．０１〜０．０５重量
％，Ｎ０．００５〜０．０２５重量％，Ｎb ０．０２〜
０．５重量％，Ｏ０．００２重量％以下，残部はＦe で
あり、１０Ｓi ＋Ｍn ＋Ｃr ≦２．０である素材であっ
て、該素材はＣ濃度が０．７〜０．９重量％となるよう
浸炭処理されており、６μｍ以下の浸炭異常層を有しか
つ♯９以上の結晶粒度を有する素材によって構成された
ことを特徴とする歯車C. 0.15 to 0.25% by weight, Si 0.1
% By weight, Mn 0.2-0.8% by weight, P0.015
Wt% or less, S0.010 to 0.015 wt%, Ni
0.4-0.6% by weight, Cr 0.2-0.8% by weight, M
o 0.6 to 1.0% by weight, Al 0.01 to 0.05% by weight, N 0.005 to 0.025% by weight, Nb 0.02 to
0.5% by weight, 0.002% by weight or less of O, the balance being Fe, and a material of 10Si + Mn + Cr≤2.0, wherein the C concentration is 0.7 to 0.9% by weight. A gear having a carburized abnormal layer of 6 μm or less and a grain size of # 9 or more.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP05117862A JP3118346B2 (en) | 1993-04-20 | 1993-04-20 | Tooth wheel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP05117862A JP3118346B2 (en) | 1993-04-20 | 1993-04-20 | Tooth wheel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH06306572A JPH06306572A (en) | 1994-11-01 |
| JP3118346B2 true JP3118346B2 (en) | 2000-12-18 |
Family
ID=14722139
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP05117862A Expired - Lifetime JP3118346B2 (en) | 1993-04-20 | 1993-04-20 | Tooth wheel |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3118346B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1128781C (en) * | 1996-07-18 | 2003-11-26 | 东丽株式会社 | Process for preparing alkyl carboxylates |
| TWI735644B (en) | 2016-11-30 | 2021-08-11 | 日商和諧驅動系統股份有限公司 | Externally toothed gear of strain wave gearing |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPWO2002053943A1 (en) * | 2000-12-27 | 2004-05-13 | 日本精工株式会社 | Toroidal continuously variable transmission |
| WO2013065718A1 (en) | 2011-11-01 | 2013-05-10 | 新日鐵住金株式会社 | Method for producing steel part |
| JP6114616B2 (en) | 2013-04-08 | 2017-04-12 | 本田技研工業株式会社 | Carburized parts, manufacturing method thereof, and steel for carburized parts |
-
1993
- 1993-04-20 JP JP05117862A patent/JP3118346B2/en not_active Expired - Lifetime
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1128781C (en) * | 1996-07-18 | 2003-11-26 | 东丽株式会社 | Process for preparing alkyl carboxylates |
| TWI735644B (en) | 2016-11-30 | 2021-08-11 | 日商和諧驅動系統股份有限公司 | Externally toothed gear of strain wave gearing |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH06306572A (en) | 1994-11-01 |
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