JPS63140068A - Spring steel having excellent fatigue strength - Google Patents
Spring steel having excellent fatigue strengthInfo
- Publication number
- JPS63140068A JPS63140068A JP28420686A JP28420686A JPS63140068A JP S63140068 A JPS63140068 A JP S63140068A JP 28420686 A JP28420686 A JP 28420686A JP 28420686 A JP28420686 A JP 28420686A JP S63140068 A JPS63140068 A JP S63140068A
- Authority
- JP
- Japan
- Prior art keywords
- inclusions
- steel
- spring
- fatigue
- spring steel
- 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.)
- Granted
Links
- 229910000639 Spring steel Inorganic materials 0.000 title claims abstract description 15
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 7
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 6
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 3
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 3
- 239000012535 impurity Substances 0.000 claims abstract 4
- 239000000203 mixture Substances 0.000 claims description 6
- 229910052742 iron Inorganic materials 0.000 claims 1
- 229910000831 Steel Inorganic materials 0.000 abstract description 18
- 239000010959 steel Substances 0.000 abstract description 18
- 238000005098 hot rolling Methods 0.000 abstract description 9
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 abstract description 4
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 abstract description 4
- 229910052593 corundum Inorganic materials 0.000 abstract description 3
- 229910045601 alloy Inorganic materials 0.000 abstract description 2
- 239000000956 alloy Substances 0.000 abstract description 2
- 229910052681 coesite Inorganic materials 0.000 abstract description 2
- 229910052906 cristobalite Inorganic materials 0.000 abstract description 2
- 239000000377 silicon dioxide Substances 0.000 abstract description 2
- 235000012239 silicon dioxide Nutrition 0.000 abstract description 2
- 229910052682 stishovite Inorganic materials 0.000 abstract description 2
- 229910052905 tridymite Inorganic materials 0.000 abstract description 2
- 230000003247 decreasing effect Effects 0.000 abstract 1
- 229910001845 yogo sapphire Inorganic materials 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 13
- 239000000463 material Substances 0.000 description 10
- 238000002844 melting Methods 0.000 description 9
- 230000008018 melting Effects 0.000 description 9
- 230000007423 decrease Effects 0.000 description 7
- 238000000034 method Methods 0.000 description 6
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 5
- 229910052802 copper Inorganic materials 0.000 description 5
- 239000010949 copper Substances 0.000 description 5
- 229920006395 saturated elastomer Polymers 0.000 description 5
- 229910052791 calcium Inorganic materials 0.000 description 4
- 229910052746 lanthanum Inorganic materials 0.000 description 4
- 229910052749 magnesium Inorganic materials 0.000 description 4
- 150000001247 metal acetylides Chemical class 0.000 description 4
- 238000009661 fatigue test Methods 0.000 description 3
- 239000000725 suspension Substances 0.000 description 3
- 229910052684 Cerium Inorganic materials 0.000 description 2
- BPQQTUXANYXVAA-UHFFFAOYSA-N Orthosilicate Chemical compound [O-][Si]([O-])([O-])[O-] BPQQTUXANYXVAA-UHFFFAOYSA-N 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 239000010431 corundum Substances 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000011086 high cleaning Methods 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 238000005491 wire drawing Methods 0.000 description 2
- 241000251468 Actinopterygii Species 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- 238000005087 graphitization Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 230000001376 precipitating effect Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000005480 shot peening Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000010561 standard procedure Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
- 150000003568 thioethers Chemical class 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Landscapes
- Springs (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
Description
【発明の詳細な説明】
[産業上の利用分野]
・本発明は、特に疲労強度の優れたばね鋼に関するもの
である。[Detailed Description of the Invention] [Industrial Application Field] - The present invention particularly relates to a spring steel with excellent fatigue strength.
[従来の技術]
従来、自動車月1等の懸架装置に用いられるばね用銅と
しては5UP6.5UP7.5UP9.5AE9254
.が主なものであった。近年自動車の軽量化が要請され
、懸架装置自体の軽量化も強く求められるようになって
きた。これに対して懸架装置全般にわたって各種の手段
が試みられているが、その中でもばねの設計応力を高く
することが効果的とされている。[Prior Art] Conventionally, 5UP6.5UP7.5UP9.5AE9254 was used as spring copper used in the suspension system of automobiles such as
.. was the main thing. In recent years, there has been a demand for lighter automobiles, and there has also been a strong demand for lighter suspension systems themselves. Various measures have been attempted for all suspension systems, among which it has been found that increasing the design stress of the spring is effective.
このような高応力設計にともない、従来の」二記ばね用
銅を素材としてばねを製作した場合、へたりが増大する
という問題が発生した。これに対処する技術として、特
開昭57−13148.特開昭58−27056、特開
昭58−27957 、特開昭58−27959 、特
開昭58−27960.特開昭58−42754 、お
よび特願昭61−38225に、耐へたり性の優れたば
ね鋼が提案されている。With such a high-stress design, when springs were manufactured using conventional copper for springs, a problem occurred in that the set-off increased. As a technique to deal with this, Japanese Patent Application Laid-Open No. 57-13148. JP-A-58-27056, JP-A-58-27957, JP-A-58-27959, JP-A-58-27960. Spring steel with excellent resistance to fatigue has been proposed in Japanese Patent Application Laid-open No. 58-42754 and Japanese Patent Application No. 61-38225.
しかしながら、これらの技術は耐へたり性に優れたばね
鋼を提供しているものの、ばね用銅として必要な疲労強
度は必ずしも十分ではない。However, although these techniques provide spring steel with excellent fatigue resistance, the fatigue strength required for copper for springs is not necessarily sufficient.
即ち、ばね用銅としては耐へたり性と共に疲労強度が要
求されている。疲労強度は材料の引張強さと共に増加す
るが、高強度材となると引張強さの増加に対する疲労強
度の増加割合は減少してくる。これは材料の高強度化に
伴って非金属介在物を主とする材料欠陥に対する疲労感
受性が高くなるためである。材料欠陥の大きさが同程度
であっても、引張強さ180Kgf/mm”程度を越え
るばね鋼であっては疲労強度の向上は困難となる。即ち
、従来許容されていた程度の大きさの非金属介在物であ
っても、材料が高強度化されたために非金属介在物の大
きさを更に小さくする必要がある。That is, copper for springs is required to have not only fatigue resistance but also fatigue strength. Fatigue strength increases with the tensile strength of the material, but when it comes to high-strength materials, the ratio of increase in fatigue strength to increase in tensile strength decreases. This is because as the strength of the material increases, the fatigue susceptibility to material defects, mainly non-metallic inclusions, increases. Even if the size of material defects is the same, it is difficult to improve the fatigue strength of spring steel with a tensile strength of more than 180 Kgf/mm. Even with nonmetallic inclusions, it is necessary to further reduce the size of the nonmetallic inclusions because the strength of the material has been increased.
従って、高い疲労強度を必要とするばね鋼において、従
来の非金属介在物は圧延工程及び伸線工程でほとんど変
化しない硬質介在物であり疲労破断の起点となっている
ことは良く知られている。Therefore, it is well known that in spring steel, which requires high fatigue strength, conventional nonmetallic inclusions are hard inclusions that hardly change during the rolling and wire drawing processes, and are the starting point of fatigue fracture. .
この対策として介在物を減少させ、さらに微細化させる
とともに軟質化することにより熱間圧延または伸線工程
でこの介在物を更に延伸させ、小型化させることが可能
である。例えば、特公昭54−7252号公報では、介
在物をスペサライトを主成分とし、A Q、0./Si
O2+A Q、03+Mn0=0.15〜0.40とす
ることが示されている。As a countermeasure to this problem, it is possible to reduce the inclusions, make them finer, and make them softer, so that the inclusions can be further stretched in the hot rolling or wire drawing process, and the size can be reduced. For example, in Japanese Patent Publication No. 54-7252, inclusions are mainly composed of spesalite, and AQ, 0. /Si
It is shown that O2+AQ,03+Mn0=0.15 to 0.40.
[発明が解決しようとする問題点]
しかしながら、前記公報に示された介在物はコランダム
を初品とする領域にまたがっているため、実際の製造に
おいては極めて硬質で有害なコランダムの発生を防止す
ることが困難であり、十分な効果が得られていない。[Problems to be solved by the invention] However, since the inclusions shown in the above-mentioned publication span the range where corundum is the initial product, it is difficult to prevent the generation of extremely hard and harmful corundum in actual manufacturing. It is difficult to do so, and sufficient effects are not obtained.
本発明の目的は、介在物を少なくすると共に、該介在物
の低融点化を図って、熱間圧延による介在物の断面縮小
を行うことにより、疲労特性の優れた高清浄度鋼を提供
することにある。An object of the present invention is to provide a high-cleanliness steel with excellent fatigue properties by reducing the number of inclusions, lowering the melting point of the inclusions, and reducing the cross section of the inclusions by hot rolling. There is a particular thing.
[問題点を解決するための手段] 本発明の要旨は。[Means for solving problems] The gist of the invention is as follows.
重量%でc : o、so〜0.80%、Si:1.0
0〜4.00%。C in weight%: o, so ~ 0.80%, Si: 1.0
0-4.00%.
Mn : 0.50〜1.50%、 Cr : Q、0
5〜1.50%であり。Mn: 0.50-1.50%, Cr: Q, 0
It is 5 to 1.50%.
カッNb:0.01〜0.50%、 V : 0.01
〜0.50%、Ti:o、oos〜0.10%、 A
Q : 0.0001〜0.05%、の1種又は2種以
上を含有し、かつCa:0.1〜20ppm 。Kak Nb: 0.01-0.50%, V: 0.01
~0.50%, Ti: o, oos ~0.10%, A
Q: 0.0001 to 0.05%, and contains one or more of the following, and Ca: 0.1 to 20 ppm.
Mg : 0.1〜20pp+m、 La+ Ce
: 0.01〜20ppmの1種又は2種以上を含有し
、かつ非金属介在物の平均的組成の構成比が。Mg: 0.1~20pp+m, La+Ce
: Contains 0.01 to 20 ppm of one or more types, and has a composition ratio of the average composition of nonmetallic inclusions.
Sin、 25〜75%。Sin, 25-75%.
Mn0 60%以下。Mn0 60% or less.
AQ、0. 35%以下、で
Mg0 40%以下
CaO50%以下、の一方又は
両方を含有することを特徴とする疲労強度の優れたばね
鋼である。AQ, 0. It is a spring steel with excellent fatigue strength characterized by containing one or both of 35% or less, Mg0, 40% or less, and CaO, 50% or less.
以下に1本発明を詳細について説明する。The present invention will be explained in detail below.
[作用]
本発明の最大の特徴は、Ca 、 M g、 L a
+ Ce 。[Action] The greatest feature of the present invention is that Ca, Mg, La
+ Ce.
の1種又は2種以上を20ppm以下の範囲で添加して
疲労性を向上させた点にある。One or more of these are added in an amount of 20 ppm or less to improve fatigue properties.
これら、Ca + M g+ L a + Ce 、は
最終の脱酸剤として、ばね鋼の清浄性を得るための元素
である。即ち、Ca、Mg、La、Ceは溶鋼中の介在
物を浮上させると共に、鋼中介在物の形状の微細化を図
る元素であり、Ca、Mgは鋼中で各々0.19901
以上で効果を示すが、20ppmを越えると、その効果
が飽和し、かつ介在物の硬質化を来し、疲労強度が低下
するので、Ca、Mg、の範囲を0.1〜20ppmと
した。La+Caは0.01ppm以上で効果を示すが
、20ppmを越えるとその効果が飽和し、かつLa及
びCeの酸化物、硫化物系の大型介在物が現れ。These, Ca + M g + La + Ce, are elements for obtaining cleanliness of spring steel as a final deoxidizing agent. That is, Ca, Mg, La, and Ce are elements that float inclusions in molten steel and refine the shape of inclusions in steel.
Although the effect is shown above, if it exceeds 20 ppm, the effect is saturated and the inclusions become hard, resulting in a decrease in fatigue strength, so the range of Ca and Mg was set to 0.1 to 20 ppm. La+Ca exhibits an effect at 0.01 ppm or more, but when it exceeds 20 ppm, the effect is saturated and large inclusions of La and Ce oxides and sulfides appear.
疲労強度を著しくて低下させるので、La+Ceの範囲
を0.01〜20ppmとした。この結果非金属介在物
の総合有量はJIS法で0.20%以下となる。該介在
物の総量が0.20%を越えると非金属介在物が巨大化
し、低融点化しても熱間圧延で該介在物の断面積を十分
縮小できない。なおこの場合のJIS法とは、 JIS
G 0555−1977 r鋼の非金属介在物の顕微
鏡試験方法」に準拠するal11定法を指すものである
。Since the fatigue strength is significantly reduced, the range of La+Ce is set to 0.01 to 20 ppm. As a result, the total amount of nonmetallic inclusions is 0.20% or less according to the JIS method. If the total amount of inclusions exceeds 0.20%, the nonmetallic inclusions become huge, and even if the melting point is lowered, the cross-sectional area of the inclusions cannot be sufficiently reduced by hot rolling. In addition, the JIS method in this case is JIS
G 0555-1977 r Refers to the al11 standard method based on the Microscopic Test Method for Nonmetallic Inclusions in Steel.
つぎに、本発明の特徴とするところは非金属介在物の量
及び種類を特定したところにあるが、これは熱間圧延中
に変形し断面積が縮小するような低融点の非金属介在物
を含有するように規定したものである。このためには、
その組成としてAQ、03−03−3jO2−系にMg
O又はCaOの一方又は両方を含ませることが必要であ
る。Next, the feature of the present invention is that the amount and type of nonmetallic inclusions are specified, and these are low melting point nonmetallic inclusions that deform during hot rolling and reduce the cross-sectional area. It is specified that it contains. For this purpose,
Its composition is AQ, 03-03-3jMg in O2- system.
It is necessary to include one or both of O or CaO.
まず、AQ203については介在物総量中に35%以下
含まれることが必要である。35%超ではアルミナ系の
介在物が多発し、疲労強度が低下する。First, AQ203 must be included in the total amount of inclusions at 35% or less. If it exceeds 35%, alumina-based inclusions occur frequently and fatigue strength decreases.
次にMnOについては介在物総量中に60%以下含まれ
ることが必要である。又60%超ではM n Oのみを
組成とする介在物が発生する。この介在物は単体で高融
点であるため、疲労強度を低下させる。Next, MnO needs to be contained in the total amount of inclusions at 60% or less. Moreover, when the content exceeds 60%, inclusions consisting only of MnO are generated. Since these inclusions alone have a high melting point, they reduce fatigue strength.
次にSiO2については介在物総量中に25〜75%含
まれることが必要である。25%未満では鋼中の酸化物
が増加し、又75%超ではSiO□系の介在物が多発し
疲労強度が低下する。Next, it is necessary that SiO2 be contained in the total amount of inclusions in an amount of 25 to 75%. If it is less than 25%, oxides in the steel will increase, and if it exceeds 75%, SiO□-based inclusions will occur frequently and the fatigue strength will decrease.
さらに、MgO又はCaOの1方又は両方を含有せしめ
ることによって、アルミナ系非金属介在物及びシリケイ
ト系非金属介在物に対してMnO系介在物と共に塩基性
成分として作用し、これらを低融点化する効果があり、
熱間圧延中の介在物断面積の縮小効果を有する。Furthermore, by containing one or both of MgO and CaO, it acts as a basic component on alumina-based nonmetallic inclusions and silicate-based nonmetallic inclusions together with MnO-based inclusions, lowering their melting point. It is effective,
It has the effect of reducing the cross-sectional area of inclusions during hot rolling.
まず、MgOを40%以下としたのは、40%以下であ
ればアルミナ系、シリケイト系の介在物に対しM n
Oと共に低融点化をもたらし、疲労向上に効果があるが
、40%超ではMgOを主とする非金属介在物が発生し
微細ではあるが、融点が高く。First, the reason why MgO is set to 40% or less is that if it is 40% or less, Mn
Together with O, it lowers the melting point and is effective in improving fatigue, but if it exceeds 40%, non-metallic inclusions mainly composed of MgO are generated, which are fine but have a high melting point.
その結果ばね鋼の疲労低下をもたらすためである。This is because this results in a decrease in fatigue of the spring steel.
次にCaOを50%以下としたのは、50%以下であれ
ばアルミナ系、シリケイト系の介在物に対しMnOと共
に低融点化をもたらし、疲労向上に効果があるが、50
%超ではCaOが主となる非金属介在物が発生し微細で
はあるが、融点が高く、その結果ばね鋼の疲労低下をも
たらすためである。Next, the reason for setting CaO to 50% or less is that if it is 50% or less, it lowers the melting point of alumina-based and silicate-based inclusions together with MnO, and is effective in improving fatigue.
%, non-metallic inclusions mainly composed of CaO are generated, which are fine but have a high melting point, resulting in a decrease in fatigue of the spring steel.
次に本発明の鋼材の成分限定理由を述べる。Next, the reason for limiting the composition of the steel material of the present invention will be described.
Cは熱処理による高応力ばね鋼として十分な強度を得る
ための元素であり、耐へたり性を確保するために0.5
0%以上必要であるが、0.80%を超えると過共析と
なり、靭性の低下が著しくなるため、その範囲を0.5
0〜0.80%とした。C is an element to obtain sufficient strength as a high stress spring steel through heat treatment, and is 0.5 to ensure resistance to fatigue.
0% or more is required, but if it exceeds 0.80%, hypereutectoid occurs and the toughness decreases significantly, so the range should be reduced to 0.5%.
The content was set at 0 to 0.80%.
つぎにSiはフェライト中に固溶することにより素地の
強度を上げると共に析出炭化物の微細化を促進し、更に
結晶粒の微細化を計るための元素であり、耐へたり性を
確保するために1.00%以上必要であるが、4.00
%を超えると延性及び靭性の低下が著しくなるため、そ
の範囲を1.00〜4.00%と定めた。特にSLの範
囲が2.5%超〜4.0%以下の範囲では高強度領域の
ばねの耐へたり性及び延性、靭性の確保の効果を有する
。Next, Si is an element that increases the strength of the matrix by solid solution in ferrite, promotes the refinement of precipitated carbides, and further refines the crystal grains, and is an element to ensure resistance to settling. 1.00% or more is required, but 4.00%
If it exceeds 1.0%, the ductility and toughness will drop significantly, so the range was set at 1.00 to 4.00%. In particular, when the SL is in the range of more than 2.5% to 4.0% or less, it has the effect of ensuring the fatigue resistance, ductility, and toughness of the spring in the high strength region.
つぎにMnは焼入れ性を高め、ばね用銅としての強度を
得るための元素であり0.5%以上必要であるが1.5
0%を超えて含有させると靭性を阻害するため、その範
囲を0.5力1ら1.50%とした。Next, Mn is an element to improve hardenability and obtain strength as copper for springs, and it is necessary to have a content of 0.5% or more, but 1.5%
If the content exceeds 0%, the toughness will be impaired, so the range was set to 0.5% to 1.50%.
更にCrは0,05%未濶ではCの黒鉛化が進み、疲労
強度を低下させるため、また1、50%超ではCrの大
きな炭化物が発生し、ばねへたり性に悪影響を与えるの
で、Crの範囲を0.05〜1.50%とした。Furthermore, if Cr is less than 0.05%, graphitization of C will progress and reduce fatigue strength, and if it exceeds 1.50%, large carbides of Cr will be generated, which will have a negative impact on spring settability. The range was set to 0.05 to 1.50%.
以上が本発明の対象とする鋼の基本成分であるが、本発
明においては前述のCa 、 M g、 L a 十C
eの外にばねの耐へたり性改善の目的でNb、V。The above are the basic components of the steel targeted by the present invention, but in the present invention, the above-mentioned Ca, Mg, La and C
In addition to e, Nb and V are added for the purpose of improving the spring's fatigue resistance.
Ti、AQの1種または2種以上を含有する。Contains one or more of Ti and AQ.
これらNb、 V、 ’ri、 A Qは結晶粒微細化
及び微細炭化物の析出によりばねへたり性を向上させる
ための元素であり、Nb、Vは各々0.01%以上で効
果を示すが0.50%を越えるとその効果が飽和し。These Nb, V, 'ri, and AQ are elements for improving spring settability by refining crystal grains and precipitating fine carbides.Nb and V each exhibit an effect at 0.01% or more, but 0. If it exceeds .50%, the effect is saturated.
Ti1i0.005%以」二で効果を示すが0.10%
を越えるとその効果が飽和し、AQは0.0001%以
上で効果を示すが0.05%を越えるとその効果が飽和
し、かつオーステナイト中に溶解されない合金炭化物が
増加し、これがばね鋼の疲労を低下させるため。Ti1i shows an effect at 0.005% or more, but 0.10%
The effect is saturated when AQ exceeds 0.0001%, but the effect is saturated when AQ exceeds 0.05%, and the amount of alloy carbides that are not dissolved in the austenite increases. To reduce fatigue.
Nb、 V(7)範囲を各々0.01〜0.50%とし
、Ti(7)範囲をo、oos〜0.10%、AQの範
囲をo、ooot〜0.05%と°した。なおこれら4
成分の合計としてはほぼ0.70%以下が望ましい。The Nb and V(7) ranges were each 0.01 to 0.50%, the Ti(7) range was o, oos to 0.10%, and the AQ range was o, ooot to 0.05%. Note that these 4
The total amount of the components is desirably approximately 0.70% or less.
本発明は上述の如く、鋼材の高清浄化を実現し、残存介
在物の微細化を実現し、更に該介在物の軟質化を実現し
た。このことにより熱間圧延工程において、更に残存す
る微細介在物の断面積を縮小2 することができ、良好
なへたり性を得ると共に、疲労強度を大幅に向上するこ
とができた。As described above, the present invention achieves high cleaning of steel materials, miniaturization of remaining inclusions, and softening of the inclusions. As a result, in the hot rolling process, it was possible to further reduce the cross-sectional area of the remaining fine inclusions, obtain good settling properties, and significantly improve fatigue strength.
[実施例] 第1表は供試鋼の化学成分を示したものである。[Example] Table 1 shows the chemical composition of the test steel.
第1表においてA1〜八8鋼は本発明例であり、B1−
86は比較材である。供試ばねは、鋼塊の鋳造後圧延比
50以上で熱間圧延、ピーリング、ばね成形し、最終硬
さ1l11c51となるように焼入れ焼戻しをおこなっ
た。In Table 1, A1-88 steels are examples of the present invention, and B1-
86 is a comparative material. The test springs were hot-rolled, peeled, and spring-formed at a rolling ratio of 50 or more after casting a steel ingot, and then quenched and tempered to a final hardness of 1l11c51.
第2表は供試ばねの諸元である。Table 2 shows the specifications of the test springs.
供試ばねはアークハイト0.5mmのショットピーニン
グを実施したのち、素線のねじり応力v wax:=
126.5kgf/am”の条件のセッチングを行った
後、ばね疲労試験を行った。The test spring was subjected to shot peening with an arc height of 0.5 mm, and then the torsional stress of the strands v wax:=
After setting the conditions of 126.5 kgf/am'', a spring fatigue test was conducted.
第3表ばばね疲労試験の結果である。Table 3 shows the results of the spring fatigue test.
第3表の結果から明らかな如く、本発明例はばね疲労試
験において全て35万回以上を達成したのに対し、比較
鋼は全て25万回未満で破断した。As is clear from the results in Table 3, all of the examples of the present invention achieved 350,000 cycles or more in the spring fatigue test, whereas all the comparative steels broke at less than 250,000 cycles.
また疲労破面にはフィッシュアイを伴う介在物が観察さ
れた。Furthermore, inclusions with fish eyes were observed on the fatigue fracture surface.
[発明の効果]
本発明は鋼材の高清浄化を実現し、残存する介在物の微
細化および軟質化を実現した。このことにより熱間圧延
で更に介在物断面の縮小化が実現した。この結果本発明
によるばねの疲労強度が著しく向上した。[Effects of the Invention] The present invention has achieved high cleaning of steel materials, and has achieved miniaturization and softening of remaining inclusions. As a result, hot rolling further reduced the cross section of inclusions. As a result, the fatigue strength of the spring according to the present invention was significantly improved.
Claims (1)
%、Mn:0.50〜1.50%、Cr:0.05〜1
.50%、であり、かつ V:0.01〜0.50%、Ti:0.005〜0.1
0%、Nb:0.01〜0.50%、Al:0.000
1〜0.05%、の1種又は2種以上を含有し、かつC
a:0.1〜20ppm、Mg:0.1〜20ppm、
La+Ce:0.01〜20ppmの1種又は2種以上
を含有し、かつ非金属介在物の平均的組成の構成比が、 SiO_2 25〜75%、 MnO 60%以下、 Al_2O_3 35%以下、で MgO 40%以下 CaO 50%以下 の一方又は両方を含み、残部はFe及び不可避的不純物
からなることを特徴とする疲労強度の優れたばね鋼。[Claims] C: 0.50-0.80%, Si: 1.00-4.00 in weight%
%, Mn: 0.50-1.50%, Cr: 0.05-1
.. 50%, and V: 0.01 to 0.50%, Ti: 0.005 to 0.1
0%, Nb: 0.01-0.50%, Al: 0.000
1 to 0.05%, and contains one or more of the following:
a: 0.1-20ppm, Mg: 0.1-20ppm,
Contains one or more of La+Ce: 0.01 to 20 ppm, and the average composition ratio of nonmetallic inclusions is: SiO_2 25 to 75%, MnO 60% or less, Al_2O_3 35% or less, and MgO A spring steel with excellent fatigue strength, characterized in that it contains one or both of 40% or less CaO and 50% or less, with the remainder consisting of Fe and unavoidable impurities.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP61284206A JPH076037B2 (en) | 1986-12-01 | 1986-12-01 | Spring steel with excellent fatigue strength |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP61284206A JPH076037B2 (en) | 1986-12-01 | 1986-12-01 | Spring steel with excellent fatigue strength |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS63140068A true JPS63140068A (en) | 1988-06-11 |
JPH076037B2 JPH076037B2 (en) | 1995-01-25 |
Family
ID=17675534
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP61284206A Expired - Lifetime JPH076037B2 (en) | 1986-12-01 | 1986-12-01 | Spring steel with excellent fatigue strength |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH076037B2 (en) |
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JPS51117115A (en) * | 1975-04-07 | 1976-10-15 | Daido Steel Co Ltd | High silcon spring steel with added ca |
JPS5713148A (en) * | 1980-06-26 | 1982-01-23 | Kobe Steel Ltd | Steel wire for suspension spring |
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1986
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JPS51117115A (en) * | 1975-04-07 | 1976-10-15 | Daido Steel Co Ltd | High silcon spring steel with added ca |
JPS5713148A (en) * | 1980-06-26 | 1982-01-23 | Kobe Steel Ltd | Steel wire for suspension spring |
JPS5732355A (en) * | 1980-08-06 | 1982-02-22 | Nippon Steel Corp | Spring steel with superior wear resistance |
JPS5735243A (en) * | 1980-08-11 | 1982-02-25 | Kyokuto Denki Kk | Hot air flow type heating apparatus |
JPS5827959A (en) * | 1981-08-11 | 1983-02-18 | Aichi Steel Works Ltd | Spring steel with superior yielding resistance |
JPS58130215A (en) * | 1982-01-27 | 1983-08-03 | Kawasaki Steel Corp | Deoxidizing method of molten steel |
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EP2163657A4 (en) * | 2007-05-25 | 2011-04-27 | Kobe Steel Ltd | Steel for high-cleanliness springs excellent in fatigue characteristics and high-cleanliness springs |
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US10526686B2 (en) | 2013-04-24 | 2020-01-07 | Nippon Steel Corporation | Low-oxygen clean steel and low-oxygen clean steel product |
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