JPS60116720A - Manufacture of spring having superior sag resistance - Google Patents
Manufacture of spring having superior sag resistanceInfo
- Publication number
- JPS60116720A JPS60116720A JP22530983A JP22530983A JPS60116720A JP S60116720 A JPS60116720 A JP S60116720A JP 22530983 A JP22530983 A JP 22530983A JP 22530983 A JP22530983 A JP 22530983A JP S60116720 A JPS60116720 A JP S60116720A
- Authority
- JP
- Japan
- Prior art keywords
- spring
- steel
- strain
- test
- resistance
- 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.)
- Pending
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/02—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for springs
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
(57)【要約】本公報は電子出願前の出願データであるた
め要約のデータは記録されません。(57) [Summary] This bulletin contains application data before electronic filing, so abstract data is not recorded.
Description
【発明の詳細な説明】
産業上の利用分野
この発明(I′i、例えば自動車の懸架ばねとして使用
される特に常温で耐へたり性に優れ、しかも耐久性1(
富むばねの製造方法に関する。DETAILED DESCRIPTION OF THE INVENTION Field of Industrial Application This invention (I'i) is used as a suspension spring for an automobile, for example, and has excellent resistance to settling at room temperature, and has durability 1 (
This invention relates to a method of manufacturing a rich spring.
自動車用等の輸送機器に使われるばねには耐へたり性、
耐久性が要求される。特に最近の自動屯業界の重要な課
題は軽量化であり懸架ばねについても軽量化の要望が強
い。Springs used in transportation equipment such as automobiles have flattening resistance,
Durability is required. In particular, weight reduction is an important issue in the automatic truck industry these days, and there is a strong desire to reduce the weight of suspension springs as well.
ばねにとって軽量化することは、ばねの負荷応力の上昇
の問題に連がる。そこで近年、高応力設計を可能にする
ために、耐へたり性と耐久性とに優れたばねが強く要望
されてきた。Reducing the weight of springs leads to the problem of increasing the load stress of the springs. Therefore, in recent years, there has been a strong demand for springs with excellent fatigue resistance and durability in order to enable high-stress designs.
ばねを繰返し圧縮して長時間使用した後、圧縮力を開放
するときに復元長さの減少を来さない性質、すなわち耐
へたり性は針設上重要な因子であるが、これは米国の自
動車について安全基準(自動車のバンパー高さの経年変
化の規定)が発端になってへたりに対する考え方が厳し
くなってきたからであった・
従来技術
耐へたり性を改善する手段としてばね鋼の高硬度化が有
効であることは周知であるが、この高硬度化はばねの早
期破壊の原因となるので実現が困難であった。ばねが早
期破壊しないためには靭性があること、すなわち耐久性
がないといけないからである。すなわちばねとしては耐
へたり性と耐久性の両性質をイjすることが必要なので
あ今。After repeatedly compressing a spring and using it for a long time, the property that the spring does not lose its resting length when the compression force is released, that is, the resistance to fatigue, is an important factor in needle installation. This is because the concept of fatigue has become stricter due to the introduction of safety standards for automobiles (regulations regarding changes in the height of automobile bumpers over time). Conventional technology High hardness of spring steel was used as a means to improve fatigue resistance. Although it is well known that hardness is effective, it has been difficult to achieve this increase in hardness because it causes early breakage of the spring. This is because in order for a spring to not break prematurely, it must have toughness, that is, durability. In other words, as a spring, it is necessary to have both properties of fatigue resistance and durability.
従来、ばねIr1fiとして要求される機械的強度を向
−]ニさせるために、炭素含有量を高めたり、種々の6
金元素を添加したりすることが試みられている。Conventionally, in order to improve the mechanical strength required for the spring Ir1fi, carbon content has been increased or various
Attempts have been made to add gold elements.
usa4sot 「ばね鋼材」には各種のばね鋼が規定
されているが、それらは耐へたり性が十分ではない。usa4sot Various spring steels are specified as "spring steel materials," but they do not have sufficient fatigue resistance.
例えば従来耐へたり性の優れたばねとしてItsSUP
7ばね鋼か多く用いられているが、懸架ばねの軽量化に
対する要求は厳しく、ll5SUP7を用いたばねより
も、さらに耐へ゛たり性の優れたばねの開発が強く望ま
れてきた。For example, ItsSUP is a spring with excellent fatigue resistance.
7 spring steel is commonly used, but there is a strong demand for lightweight suspension springs, and there has been a strong desire to develop a spring with even better wear resistance than springs using ll5SUP7.
発明の目的
本発明は上記業界の要望に応え、耐へだり性において従
来のばねよりも遥かに優れ、しかも耐久性を兼備するば
ねの製造方法の開発を目的とする。OBJECTS OF THE INVENTION In response to the above-mentioned needs of the industry, the present invention aims to develop a method for manufacturing a spring that is far superior in sagging resistance to conventional springs and is also durable.
発明の構成
一般に、鋼を冷間加工し、その後荷重を除去して時効さ
せることを歪時効と云うが、本発明者は種々の研究実験
により、ばね鋼を歪時効処理することが降伏点を上昇さ
せて耐へたり性を改善する上で極めて有効であるこを見
出しだ・
ばね鋼の歪時効処理の効果を十分に発揮するには、鋼に
Nを添加し且つ酸可溶性(Sojl)AAを低く抑える
ことによって鋼中の固溶Nを増大させることが重要であ
り、Nが鋼中に固溶Nとして存在することが冷間加工に
よって導入された転位を固定させ、効果的に降伏点を上
昇させる。Structure of the Invention In general, the process of cold working steel, then removing the load and aging it is called strain aging. Through various research experiments, the present inventor has found that strain aging treatment of spring steel can lower the yield point. It has been found that this is extremely effective in increasing the strain aging properties of spring steel and improving its fatigue resistance.In order to fully demonstrate the effects of strain aging treatment on spring steel, it is necessary to add N to the steel and add acid-soluble (Sojl) AA to the steel. It is important to increase the solid solution N in steel by keeping it low, and the presence of N in the steel as solid solution fixes dislocations introduced by cold working, effectively lowering the yield point. raise.
AlばNとの親和力が大きいので、Alが鋼中に存在す
るとAINとなり、Nを固定して」1記Nの降伏点を上
昇させる効果を減少させる。これよりしてA7I含有量
を低減させることによって固溶Nを増大させ得るとの知
見を得た。Since Al has a large affinity with N, when Al exists in steel, it becomes AIN, which fixes N and reduces the effect of increasing the yield point of N in 1. From this, it was found that solid solution N could be increased by reducing the A7I content.
もう一つの知見は鋼中酸素を減少させる点である。上記
の固溶N増大による歪時効処理は耐へたり性を改善する
ことに有効であるか、反面ばねを脆くし、早期折損の原
因となる問題がある。Another finding is that it reduces oxygen in steel. Although the above-mentioned strain aging treatment by increasing solid solution N is effective in improving the fatigue resistance, there is a problem in that it makes the spring brittle and causes early breakage.
本発明者は鋼中の酸化物系介在物を低減させることかこ
の早期折損の問題を解決する手段として効果的であるこ
と、すなわち鋼中に存在する酸化物系介在物が疲労破壊
あるいは脆性破壊の起点になるので、これを1成域させ
ることが高硬度下での靭性を増大させ、その結果、耐久
性を向上させる手段となることを確認した。The present inventor discovered that reducing oxide inclusions in steel is an effective means of solving this problem of early breakage. Therefore, it was confirmed that making this one region increases toughness under high hardness, and as a result, it becomes a means to improve durability.
なおまた前記基本元素の池に、ばねの用途、要求性能に
応じてS i、 Cr、 V、 Nb、 Bの各種元素
の1種あるいは1種以上を添加することにより耐へたり
性、耐久性の一層殴れるばねの製作が1げ能となる。Furthermore, the fatigue resistance and durability can be improved by adding one or more of various elements such as Si, Cr, V, Nb, and B to the basic element pond according to the application and required performance of the spring. The first step is to create a spring that can be hit even harder.
既述のとおり、本発明の方法は歪時効によりばねの1(
11jへたり性を改善する点に特徴を有するものである
。然してこの歪時効処理は、何等特殊な工程を導入する
ことなく、通常のばね製造工程で実施される冷間セツテ
ィング(歪の導入)、および塗装後の乾燥熱(時効処理
)によっても有効に行われffl、るのであるが、本発
明者はさらに実験の結果、冷間歪の導入量および時効温
度に一定の制限を設けることによって、耐へたり性に一
層優れた効果をもつばねが得られることを発見した。As mentioned above, the method of the present invention reduces the stress of the spring by strain aging.
11j is characterized in that it improves the settling property. However, this strain aging treatment can also be effectively performed by cold setting (introducing strain) carried out in the normal spring manufacturing process and drying heat (aging treatment) after painting, without introducing any special process. However, as a result of further experiments, the present inventor found that by setting certain limits on the amount of cold strain introduced and the aging temperature, a spring with even better fatigue resistance could be obtained. I discovered that it can be done.
本発明はこれらの知見に基〈もので、
C: 0.50−0.70%、Mn : 0.50−1
.50%、Ni:0.010−0.020%、5o71
An : 0.010 %以下、鋼中O:0.002チ
以下で、更に必要に応じ、Si : 0.50〜2.5
0%。The present invention is based on these findings, C: 0.50-0.70%, Mn: 0.50-1
.. 50%, Ni: 0.010-0.020%, 5o71
An: 0.010% or less, O in steel: 0.002% or less, and if necessary, Si: 0.50 to 2.5
0%.
V:0.02〜0.30係、Nb:0.01〜0.30
%のL種または2種以上、Cr : 0.20−1.0
% 、 B : 0.0005−0.0040チの1種
または両種、の一方または双方を含み。V: 0.02-0.30, Nb: 0.01-0.30
% L type or 2 or more types, Cr: 0.20-1.0
%, B: 0.0005-0.0040, or both.
残部はFeおよび不可避的不純物よりなる鋼をコイルに
成形し、これに残留歪o、io〜1.0%を与えるよう
に冷間セツティングを施し、しかる後150〜300’
Cに加熱処理を行うことを特徴とする耐へだり性の優れ
たばねの製造方法を要旨とする。Steel, the remainder of which is Fe and unavoidable impurities, is formed into a coil, subjected to cold setting to give a residual strain o, io ~1.0%, and then set at 150 to 300'.
The gist of this invention is a method for manufacturing a spring with excellent sag resistance, which is characterized by subjecting C to heat treatment.
次に上記の如く成分の範囲および構成要件を特定した理
由を説明する。Next, the reason for specifying the range of components and constituent requirements as described above will be explained.
C:Cはばね強度を得るのに必須の成分である。C: C is an essential component to obtain spring strength.
0.50%未満では十分な強度が得られず、0.70%
を超えては靭性が阻害される。If it is less than 0.50%, sufficient strength cannot be obtained;
Exceeding this will impede toughness.
Mn:Mnは鋼に焼入性を付与するのに必須の成分であ
る。0.50%未満では十分な効果が得られず、1.5
0係を超えると焼入性が過大となるだけでなく、靭叶が
1≦1」害される。Mn: Mn is an essential component for imparting hardenability to steel. If it is less than 0.50%, sufficient effect cannot be obtained;
If the ratio exceeds 0, not only will the hardenability become excessive, but the toughness will be damaged by 1≦1.
NUNは鋼中で遊離Nとして歪時効を促進させる。NUN accelerates strain aging in steel as free N.
0.010%未満では十分な効果が得られず、0.02
0係を超えると時効効果が過大となり靭性を劣化させる
。If it is less than 0.010%, sufficient effect cannot be obtained;
When the coefficient exceeds 0, the aging effect becomes excessive and the toughness deteriorates.
5oesAex鋼中に酸可溶性A6として存在すると、
A7!NとしてNを固定してNの歪時効に対する効果を
減殺するのでo、oto%以下に管理する必要がある。When present as acid-soluble A6 in 5oesAex steel,
A7! Since N is fixed as N and the effect of N on strain aging is reduced, it is necessary to manage it to less than o, oto%.
鋼中0:鋼中0は鋼中にて酸化物介在物として存在し、
破壊靭性を劣化させて疲労破壊の原因となる0、002
0%以下にすることによって酸化物介在物は大巾に減少
し、破壊靭性を改善して耐久性を向−ヒさせるため、歪
時効による耐久性の劣化を防止できる。なお酸素の低減
は例えば製鋼工程での脱ガス処理、あるいは真空溶解等
で達成することができる。0 in steel: 0 in steel exists as oxide inclusions in steel,
0,002 which deteriorates fracture toughness and causes fatigue fracture.
By setting the content to 0% or less, oxide inclusions are greatly reduced, improving fracture toughness and increasing durability, thereby preventing deterioration of durability due to strain aging. Note that the reduction in oxygen can be achieved, for example, by degassing treatment in the steel manufacturing process or vacuum melting.
Ct:W4に焼入性の付与および脱炭層生成の抑制(炭
素の活量を低下)175両方の効果をもつ。ばねの線径
が太くて基礎成分では焼入性が不足する場合に、線径に
応じて添加する。0.20%未満では焼入性の付与、脱
炭層生成の抑制の効果が十分でな(,1,0係を超えて
添加しても効果の改善はみられない。Ct: Has the effect of imparting hardenability to W4 and suppressing the formation of a decarburized layer (reducing carbon activity)175. When the wire diameter of the spring is large and the hardenability is insufficient with the basic ingredients, it is added according to the wire diameter. If it is less than 0.20%, the effect of imparting hardenability and suppressing the formation of a decarburized layer will not be sufficient (and even if it is added in an amount exceeding 1.0%, no improvement in the effect will be seen.
B:低温焼戻時に鋼の破壊靭性を改善する。鋼中Oの減
少と同様、歪時効による耐久性の劣化を防止する。0.
、OOO5%未満では十分な効果が得られず、0.00
40%を超えて添加しても効果の改善はみられない。B: Improves the fracture toughness of steel during low temperature tempering. As well as reducing O in steel, it prevents deterioration of durability due to strain aging. 0.
, if OOO is less than 5%, sufficient effect cannot be obtained, and 0.00
Even if it is added in excess of 40%, no improvement in the effect is observed.
St 、V、Nb : Si 、V、Nbはその中から
1種または2種以上を選択使用できる元素である。V、
Nbは鋼中で炭化物として存在し、結晶粒を微細化する
ことにより、Slは焼戻時に析出する炭化物を微細均一
化することにより、耐へたり性を改善する。基礎成分鋼
の耐へたり性をさらに増強する場合に添加する。Siは
0.50%未満は通常の脱酸剤として不可避的に混入す
る。0.50%以上の添加により耐へたり性の効果が得
られる。2.50%を超えて添加しても効果の改善はみ
られず、逆に熱処理時の脱炭層の生成が顕著になる。■
は0.02チ、Nbは0.01俤を下回ると十分な上記
効果は得られず、共に0.30%を超えても効果の改善
はみられず高価となるだけである。St, V, Nb: Si, V, and Nb are elements from which one or more types can be selected and used. V,
Nb exists as a carbide in the steel, and by refining the crystal grains, Sl improves the settling resistance by making the carbides that precipitate during tempering fine and uniform. Added to further enhance the sag resistance of the basic component steel. Less than 0.50% of Si is unavoidably mixed as a normal deoxidizing agent. By adding 0.50% or more, the effect of sagging resistance can be obtained. Even if it is added in an amount exceeding 2.50%, no improvement in the effect is observed, and on the contrary, the formation of a decarburized layer during heat treatment becomes noticeable. ■
If Nb is less than 0.02% and Nb is less than 0.01%, the above effect cannot be obtained sufficiently, and even if both exceed 0.30%, no improvement in the effect will be seen and the price will only increase.
なお鋼中に不可避的に混入する不純物については、Pを
0.015チ以下、Sを0.010チ以下sTtを0.
005%以下に調整することも鋼の破壊靭性を改善する
手段として有効である。またばね鋼を熱処理して使用す
るときは焼入性のよいこと、鋼の表面に生ずる脱炭層を
薄くすることが耐久性を保つのに必要である。Regarding impurities that inevitably enter the steel, P is 0.015 inches or less, S is 0.010 inches or less, and sTt is 0.
Adjustment to 0.005% or less is also effective as a means of improving the fracture toughness of steel. Furthermore, when using heat-treated spring steel, it is necessary to have good hardenability and to make the decarburized layer formed on the surface of the steel thin in order to maintain durability.
次に冷同セツティングによる歪の導入量および加熱処理
すなわち塗装後の乾燥温度についてであるが、本発明者
は冷間歪の導入量および時効温度の影響を調査するため
に挾りクリープ試験を実施した。ばねのへたりは一種の
クリープ現象とされ、耐へたり性は涙りクリープ試験に
よって評価することができる。Next, regarding the amount of strain introduced by cold setting and the drying temperature after heat treatment, the present inventor conducted a pinch creep test to investigate the effect of the amount of cold strain introduced and aging temperature. carried out. Spring fatigue is considered to be a type of creep phenomenon, and the fatigue resistance can be evaluated by a tear creep test.
第1図、第2図に該試験の結果を示す。The results of this test are shown in FIGS. 1 and 2.
この試験の供試試料は後述実施例の項第1表に記載の試
料lおよびlOである。The test samples for this test are Samples 1 and 1O listed in Table 1 in the Examples section below.
供試資料は20問直径に鍛伸した後半打部を11趨直径
の試験片に粗加工の後、焼入焼戻処理してロックウェル
C硬度51 (HRC51)に調整した後半打部IQm
直径の試験片に仕上加工した。The test material is the second half hammer part IQm, which was forged to a diameter of 20, roughly processed into a test piece of 11 diameters, and then quenched and tempered to have a Rockwell C hardness of 51 (HRC51).
It was finished into a diameter test piece.
第1図は冷間歪の導入量について調査した結果であり、
上記試験片にO〜1.5チの捩り歪を加え、さらに20
0“CX 30 mii’nの時効処理したものについ
ての結果である。Figure 1 shows the results of an investigation into the amount of cold strain introduced.
A torsional strain of 0 to 1.5 inches was applied to the above test piece, and a further 20
These are the results for aged 0"CX 30 mii'n.
冷間歪の導入量を0.101以上にすることにより、9
6hr後のクリープ歪は大巾に減少して優れた耐へたり
性を示していることが判る。ところで実際 、のバネの
セツティング作業において1.0%を超えて残留歪を与
えることは、ばねのコイリング時に過大なピッチ角を要
し、セツティングの時にばねの座屈の原因となるので好
ましくない。従って残留歪の値を0.lO〜1.0俤の
範囲に選定した。By increasing the amount of cold strain introduced to 0.101 or more, 9
It can be seen that the creep strain after 6 hours was significantly reduced, indicating excellent resistance to settling. However, in reality, it is preferable to apply a residual strain of more than 1.0% in the spring setting process, as this will require an excessive pitch angle when coiling the spring, which may cause buckling of the spring during setting. do not have. Therefore, the value of residual strain is set to 0. The range was selected to be between 10 and 1.0 yen.
第2図は時効温度の影響を調査した結果である。Figure 2 shows the results of investigating the influence of aging temperature.
焼入・焼戻処理によりHRC51に調整した前記供試片
に0.2 %の換り歪を加え、さらに100〜350’
CX 30 minの時効処理したものについての結果
である。150〜300℃の時効処理をすることによリ
、96h【 後のクリープ歪は大巾に減少し優れた耐へ
たり性を有していることを示している。まだ300°C
を超える時効温度でクリープ歪が増大する。A strain of 0.2% was added to the specimen, which had been adjusted to HRC51 by quenching and tempering, and then further strained to 100 to 350'.
These are the results for those subjected to aging treatment for CX 30 min. By aging at 150 to 300°C, the creep strain after 96 hours was significantly reduced, indicating that it has excellent resistance to settling. Still 300°C
Creep strain increases at aging temperatures exceeding .
これはセツティングにより生じだ表向の圧縮残留応力が
低ドすることによるものと(毘定され、従って時効を品
度処理範囲を1.50〜300’Cに設定した。It was determined that this was due to the lower compressive residual stress on the surface produced by the setting, and therefore the aging and quality treatment range was set at 1.50 to 300'C.
実tイa1クリl
第1表に供試試料のflZ学成分成分す、試料1−13
は本発明成分範囲で、N含有量および酸可溶性N(So
e−Ae)含有量をそれぞれ0.010−0.020係
および(1,010%以下に調整し、酸素含有量(鋼中
0)を0.0020%以下に調整しである。比較試料1
4〜16はJISSOP7相当の従来のばねで5olJ
−Alが、高い場合(試刺番り・14.16)と鋼中0
の高い場合(試料番り°15)で、いずれも本発明の成
分範囲外のものである。Table 1 shows the flZ chemical components of the test samples, Sample 1-13.
is the component range of the present invention, N content and acid-soluble N (So
e-Ae) content was adjusted to 0.010-0.020% and (1,010% or less, respectively), and the oxygen content (0 in steel) was adjusted to 0.0020% or less. Comparative sample 1
4 to 16 are conventional springs equivalent to JISSOP7, 5olJ
- When Al is high (testing number: 14.16) and 0 in steel
(sample number: 15°), all of which are outside the component range of the present invention.
第2表に各供試試料についての捩ルクリープ試験、シャ
ルピー衝撃試験、焼入硬度試験、脱炭試験の結果を示す
。Table 2 shows the results of the torsional creep test, Charpy impact test, quenching hardness test, and decarburization test for each sample.
挨りクリープ試験は前述のロックウェルC硬度・HRC
51の゛に打部10m直径の試験片にばねのセツティン
グの歪に相当する0、2チの換り歪を加え、さらに塗装
後の乾燥に相当する200°CX30m1nの時効処理
を施し、表面剪断応力τ−110kg1/mAの候り応
力を加え常温96 hr後のクリープ歪の結果を示した
。ばねのへたりは一種のクリープ現象とされ、耐へたり
性はこの結果により評価できる。The dust creep test is based on the aforementioned Rockwell C hardness/HRC.
A test piece with a diameter of 10 m at the striking part was subjected to 0 or 2 inches of displacement strain, which corresponds to the strain of spring setting, and was then subjected to an aging treatment of 200°C x 30 m1n, which corresponds to drying after painting. The results of the creep strain after applying a shear stress τ-110 kg1/mA of creeping stress and 96 hours at room temperature are shown. Spring fatigue is considered to be a type of creep phenomenon, and the fatigue resistance can be evaluated based on this result.
シャルピー衝撃試験は、供試試料を20鴫直径に鍛伸し
た後に11mm角に粗加工後、焼入焼戻処理してHRC
51に調整した後、JISa号試験片に仕にげして常温
で試験した。その結果は衝撃値で示され、供試試料の靭
性が評価できる。In the Charpy impact test, the test sample was forged to a diameter of 20 mm, then roughly machined to 11 mm square, and then quenched and tempered.
After adjusting the temperature to 51, it was applied to a JISa test piece and tested at room temperature. The results are shown as impact values, and the toughness of the test sample can be evaluated.
焼入硬度試験は、供試試料を鍛伸後10m直径および2
0I+ll11直径に機械加工し、900°CX30分
加熱後油焼入した後、表面硬度を測定した。これにより
供試試料の焼入性が評価できる。In the quenching hardness test, the test sample was forged and stretched with a diameter of 10 m and a
It was machined to a diameter of 0I+ll11, heated at 900° C. for 30 minutes, and then oil quenched, and then its surface hardness was measured. This allows the hardenability of the test sample to be evaluated.
脱炭試験は供試試料の鍛伸後、lOa直径に機械加工し
、900°cx3分あるいは900°Cx1O分の加熱
後、油焼入し、表面の脱炭層深さを顕微鏡にて測定シ、
ソノ結果をDm−T(JISG 0558による)で示
した。これにより供試試料の脱炭抑制効果が評価できる
。In the decarburization test, the sample was forged and stretched, machined to a diameter of 1Oa, heated at 900°C for 3 minutes or 900°C for 10 minutes, oil quenched, and the depth of the decarburized layer on the surface was measured using a microscope.
The test results are shown as Dm-T (according to JISG 0558). This allows evaluation of the decarburization suppression effect of the test sample.
本発明範囲の試料はいずれも比較試料14.16に較べ
少ないクリープ歪を示しており、良好な耐へだり性を有
していることがわかる。特にSi、V。It can be seen that all the samples within the scope of the present invention exhibit less creep strain than Comparative Samples 14 and 16, and have good sag resistance. Especially Si, V.
Nbを単独あるいは複合添加した試料2,4.6,8゜
9.10,11.12.13 はすぐれた耐へだり性を
示すO
靭性についても低酸素鋼である本発明範囲の試料はいず
れも比較試料より良好な衝撃値を示している。比較試料
の中で、試料15はN%A8が本発明の成分範囲に入っ
ているため、耐へだり性は良好であるが、酸素が高く、
靭性が低いため実際のばハへの適用は困難である。本発
明範囲の試料の中でBを添加した資料5.6,7.8,
12.13は特に優れた靭性を示している。Samples 2, 4.6, 8゜9.10, 11.12.13 with Nb added alone or in combination exhibit excellent sag resistance. Also shows a better impact value than the comparative sample. Among the comparative samples, sample 15 has good sag resistance because N%A8 is within the component range of the present invention, but it has a high oxygen content.
Due to its low toughness, it is difficult to apply it to actual Bahamas. Materials 5.6, 7.8, with B added among the samples within the scope of the present invention,
12.13 shows particularly excellent toughness.
第2表には焼入性に及ぼすCrの影響も示されている。Table 2 also shows the influence of Cr on hardenability.
本発明範囲の試料、比較試料ともにlOφサンプルでは
十分な焼入硬度が得られているものの、20φサンプル
についてt/′iCrを添加した試料3.4,7,8,
10.11.13のみが良好な焼入硬度を示している。Although sufficient quenching hardness was obtained for the lOφ sample for both the samples within the scope of the present invention and the comparative samples, for the 20φ sample, samples 3.4, 7, 8 with t/′iCr added,
Only No. 10.11.13 shows good quench hardness.
すなわち、大径ばねに対してはCrを添加ノーることか
有効である。In other words, it is effective not to add Cr to large diameter springs.
さらに脱炭肋性についてみると、比較試料14゜15+
16は加熱時間がio分になると顕著な脱炭を示してお
り、ばね製造の際に加熱時間等過大な管理を要すること
がわかる。然るに本発明範囲の試料10は比較試料と同
水準の81を含有しているものの、Crを同時添加する
ことにより脱炭抑制の効果が顕著であり、高Sij賛で
のCrの添加の有効性が示されている。Furthermore, looking at the decarburization properties, the comparison sample 14゜15+
No. 16 showed remarkable decarburization when the heating time reached io minutes, indicating that excessive management of the heating time, etc., was required during spring manufacture. However, although sample 10 in the scope of the present invention contains 81 at the same level as the comparative sample, the simultaneous addition of Cr has a remarkable effect of suppressing decarburization, and the effectiveness of Cr addition at high Sij conditions. It is shown.
第 3 表
第 4 表
実施例2
本発明の有効性をさらに確認するだめ、実体コイルばね
を試作し動的へたり試験を実施した。Table 3 Table 4 Example 2 In order to further confirm the effectiveness of the present invention, a prototype solid coil spring was manufactured and a dynamic fatigue test was conducted.
前記第1表の試料1,10,11.L4..15 の鋼
を用いて第3図に示す工程で第3表に示す諸元のばねを
製作し、平均応力65kyf/ma、応力振巾50kg
4/mAになるように常温で200,000回繰返し応
力を与へた後のへたりを測定した。その結果を第4表に
示す・同表はへたりを残留剪断歪量で表示したものであ
る・本発明範囲の試料で製作したばねはいずれも比較試
料14で製作したばねより少なりへたり量を示し、特に
試料10および11のばねは非常に優れた耐へたり性を
示している。なお試料15は、5olJ−A7I、Nは
本発明の範囲内であるか鋼中Oか高く、そのためこのば
ねは試験中に折1itした。Samples 1, 10, 11 in Table 1 above. L4. .. A spring with the specifications shown in Table 3 was manufactured using No. 15 steel in the process shown in Figure 3, with an average stress of 65 kyf/ma and a stress amplitude of 50 kg.
The fatigue was measured after applying stress 200,000 times at room temperature so that the stress was 4/mA. The results are shown in Table 4. ・The table shows the set-off in terms of the amount of residual shear strain. ・The springs manufactured using the samples within the scope of the present invention all have less set-off than the springs manufactured using comparative sample 14. In particular, the springs of samples 10 and 11 show very good resistance to fatigue. In sample 15, 5olJ-A7I,N was within the range of the present invention or higher than O in steel, so this spring was broken during the test.
発明の効果
不発[1」方法により製造されるばねは、上述の如く、
極めて良好な聞・1へたり性と耐久性を兼備するので、
車輌等の軽量化や資材の節約等に貢献するところが大で
ある。Effects of the invention [1] The spring manufactured by the method is as described above.
Because it has extremely good wear resistance and durability,
This greatly contributes to reducing the weight of vehicles and saving materials.
第1図は、候りクリープ歪に及ぼす冷間歪導入iトの影
響を示す曲線図。第2図は、捩りクリープ歪に及ばず時
効処理温度の影響を示す曲線図。第3図は、コイルばね
の製作工程図である。
出 願 人 住友金属工業株式会社
第 1 図
一沖づ情i喜入量(%)
第 2 図
→B! タカ、均、工叉温農ぐC)
第3図FIG. 1 is a curve diagram showing the influence of cold strain introduction on cold creep strain. FIG. 2 is a curve diagram showing the influence of aging treatment temperature on torsional creep strain. FIG. 3 is a manufacturing process diagram of the coil spring. Applicant: Sumitomo Metal Industries, Ltd. No. 1 Fig. 1 Input amount (%) Fig. 2 → B! Figure 3
Claims (1)
50〜1.50%、N:0.010−0.020%、S
oトAjl : 0.010S以下、鋼中0:0.00
2チ以下で、更に必要に応じ、Si: 0.50−2.
50%、 V : 0.02−0.30% 、Nb :
0.01−0.30% O1種または2種以上、Cr
: 0.20”1.0% 、 B :0.0005〜
0.0040チの1種または両種、の一方または双方を
含み、残部はFeおよび不可避的不純物よりなる鋼をコ
イルに成形し、これに残留歪0.10〜i、o sを与
えるように冷間セツティングを施し、しかる後150〜
300°Cに加熱処理を行うことを特徴とする耐へたり
性の浸れたばねの製造方法。(1) C: 0.50-0.70%, Mn: 0.
50-1.50%, N: 0.010-0.020%, S
otoAjl: 0.010S or less, 0:0.00 in steel
2 inches or less, and if necessary, Si: 0.50-2.
50%, V: 0.02-0.30%, Nb:
0.01-0.30% O1 type or 2 or more types, Cr
: 0.20"1.0%, B: 0.0005~
A steel containing one or both of 0.0040 and 0.0040 and the remainder consisting of Fe and unavoidable impurities is formed into a coil, so as to give a residual strain of 0.10 to i, o s. After cold setting, 150~
A method for manufacturing a soaked spring with resistance to settling, characterized by heat treatment at 300°C.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP22530983A JPS60116720A (en) | 1983-11-28 | 1983-11-28 | Manufacture of spring having superior sag resistance |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP22530983A JPS60116720A (en) | 1983-11-28 | 1983-11-28 | Manufacture of spring having superior sag resistance |
Publications (1)
Publication Number | Publication Date |
---|---|
JPS60116720A true JPS60116720A (en) | 1985-06-24 |
Family
ID=16827326
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP22530983A Pending JPS60116720A (en) | 1983-11-28 | 1983-11-28 | Manufacture of spring having superior sag resistance |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS60116720A (en) |
Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS63274739A (en) * | 1987-04-30 | 1988-11-11 | Aichi Steel Works Ltd | Steel for spring having excellent hardenability and durability |
JPS6483644A (en) * | 1987-09-25 | 1989-03-29 | Nissan Motor | High-strength spring |
JPH06220584A (en) * | 1992-11-24 | 1994-08-09 | Stelco Inc | Steel composition for suspension spring |
JP2008266782A (en) * | 2007-03-23 | 2008-11-06 | Aichi Steel Works Ltd | Spring steel with excellent hydrogen embrittlement resistance and corrosion fatigue strength, and high-strength spring parts using the same |
KR20210036916A (en) * | 2018-07-27 | 2021-04-05 | 바오샨 아이론 앤 스틸 유한공사 | Spring steel with excellent fatigue life and its manufacturing method |
-
1983
- 1983-11-28 JP JP22530983A patent/JPS60116720A/en active Pending
Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS63274739A (en) * | 1987-04-30 | 1988-11-11 | Aichi Steel Works Ltd | Steel for spring having excellent hardenability and durability |
JPS6483644A (en) * | 1987-09-25 | 1989-03-29 | Nissan Motor | High-strength spring |
JPH06220584A (en) * | 1992-11-24 | 1994-08-09 | Stelco Inc | Steel composition for suspension spring |
JP2008266782A (en) * | 2007-03-23 | 2008-11-06 | Aichi Steel Works Ltd | Spring steel with excellent hydrogen embrittlement resistance and corrosion fatigue strength, and high-strength spring parts using the same |
KR20210036916A (en) * | 2018-07-27 | 2021-04-05 | 바오샨 아이론 앤 스틸 유한공사 | Spring steel with excellent fatigue life and its manufacturing method |
US20210164078A1 (en) * | 2018-07-27 | 2021-06-03 | Baoshan Iron & Steel Co., Ltd. | Spring steel having superior fatigue life, and manufacturing method for same |
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