JPH05148581A - Steel for high strength spring and production thereof - Google Patents
Steel for high strength spring and production thereofInfo
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- JPH05148581A JPH05148581A JP34001291A JP34001291A JPH05148581A JP H05148581 A JPH05148581 A JP H05148581A JP 34001291 A JP34001291 A JP 34001291A JP 34001291 A JP34001291 A JP 34001291A JP H05148581 A JPH05148581 A JP H05148581A
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- spring
- strength
- spring steel
- strength spring
- steel
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Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、内燃機関の弁ばねや懸
架ばね等に使用される高強度ばね用鋼および上記用途に
最適な高強度ばねの製造方法に関し、特に材料強度が20
0kgf/mm2以上であり、しかもばね特性として要求される
疲労寿命およびへたり特性を十分に満足することのでき
る高強度ばねの製造方法およびその様な高強度ばねを製
造する為のばね用鋼に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to steel for high strength springs used for valve springs, suspension springs, etc. of internal combustion engines and a method for manufacturing high strength springs most suitable for the above-mentioned uses.
A method for producing a high-strength spring which is 0 kgf / mm 2 or more and is capable of sufficiently satisfying the fatigue life and the sag characteristic required as spring characteristics, and a spring steel for producing such a high-strength spring. It is about.
【０００２】[0002]
【従来の技術】ばね用鋼の化学成分はJIS G3565 〜G356
7, G4801等に規定されており、それから製造された圧延
材に対して所定の線径まで伸線加工し、その後オイルテ
ンパー処理後ばね加工（冷間成形ばね）したり、圧延材
を伸線加工した後、加熱してばね成形した後焼入れ焼戻
し（熱間成形ばね）を行なうこと等により、各種ばねが
製造されている。近年ばねに対する要求が次第にきびし
くなるにつれ、各種の合金鋼に夫々熱処理を施したもの
が多く利用されている。[Prior Art] Chemical composition of spring steel is JIS G3565 to G356
7, G4801 etc., and the rolled material manufactured from it is drawn to a predetermined wire diameter, then oil tempered and then spring processed (cold forming spring), or the rolled material is drawn. After processing, various springs are manufactured by heating and spring forming, and then quenching and tempering (hot forming spring). As the demand for springs has become increasingly severe in recent years, various alloy steels that have undergone heat treatment are widely used.
【０００３】従来のばね鋼においては、焼入れ焼戻し後
の強度が160 〜190kgf/mm2程度であるのが一般的である
が、強度が200kgf/mm2以上の高強度ばね用鋼が要求され
る様になってきた。一方ばねの重要特性としては、高い
疲労寿命および耐へたり性が要求される。高疲労寿命を
得るために、冷間および熱間でショットピーニングが施
される。また良好な耐へたり性を得るために、製造の終
りの方の工程でセッチングが行なわれる。しかしながら
従来のばね用鋼では、強度、疲労寿命およびへたり特性
のすべてを満足することはできなかった。In the conventional spring steel, the strength after quenching and tempering is generally about 160 to 190 kgf / mm 2 , but a high strength spring steel having a strength of 200 kgf / mm 2 or more is required. It has become like. On the other hand, important fatigue properties of springs are high fatigue life and sag resistance. Shot peening is performed cold and hot to obtain high fatigue life. Further, in order to obtain a good sag resistance, the setting is performed in the process at the end of manufacturing. However, conventional spring steels have not been able to satisfy all of strength, fatigue life and fatigue characteristics.
【０００４】[0004]
【発明が解決しようとする課題】本発明はこの様な事情
に着目してなされたものであって、その目的は、強度が
200kgf/mm2以上であり、しかも疲労特性およびへたり特
性も良好な高強度ばねを製造する方法およびその様な高
強度ばねを得る為のばね用鋼を提供することにある。SUMMARY OF THE INVENTION The present invention has been made in view of such circumstances, and its purpose is to improve strength.
It is an object of the present invention to provide a method for producing a high-strength spring having a fatigue strength and a sag characteristic of 200 kgf / mm 2 or more and a spring steel for obtaining such a high-strength spring.
【０００５】[0005]
【課題を解決するための手段】上記目的を達成し得た本
発明の高強度ばね用鋼とは、Ｃ：0.35〜0.65％，Ｓｉ：
１〜３％，Ｍｎ：0.5 〜２％，Ｎｉ：４％以下，Ｃｒ：
２超〜３％，Ｍｏ：0.05〜１％，Ｖ：0.05〜0.5 ％を夫
々含有し、残部鉄および不可避不純物からなる点に要旨
を有するものである。本発明に係る高強度ばね用鋼は、
上記の元素を基本成分とするものであるが、必要に応じ
てＮｂ，Ｔｉ，Ａｌ，Ｂ，Ｗ，Ｃｕ等を含有するもので
あってもよい。The high-strength spring steel of the present invention capable of achieving the above object is C: 0.35 to 0.65%, Si:
1-3%, Mn: 0.5-2%, Ni: 4% or less, Cr:
It has a gist in that it contains more than 2 to 3%, Mo: 0.05 to 1%, V: 0.05 to 0.5%, and the balance is iron and inevitable impurities. High-strength spring steel according to the present invention,
Although the above-mentioned elements are used as basic components, they may contain Nb, Ti, Al, B, W, Cu, etc., if necessary.
【０００６】また上記の様な各種ばね用鋼を用い、(1)
熱間ばね成形後焼入れ焼戻し処理を施し、更にセッチン
グおよびショットピーニングを施すこと、または(2) オ
イルテンパー処理を施した後、冷間ばね成形し、更にセ
ッチングおよびショットピーニングを施すこと、等によ
って希望する特性の高強度ばねが得られる。In addition, using various spring steels as described above, (1)
Desired by performing quenching and tempering treatment after hot spring forming, then setting and shot peening, or (2) after oil tempering, cold spring forming, further setting and shot peening, etc. A high-strength spring having the characteristics described above can be obtained.
【０００７】[0007]
【作用】ばねの疲労寿命を向上させるためには、素材の
靭性向上を図る必要がある。本発明者らは高強度を維持
しつつ靭性向上の図れるＣ範囲として、0.35〜0.65％を
選んだ。そしてこの範囲におけるへたり特性を改善する
手段について様々な角度から検討したところ、特にＣｒ
は耐へたり性を向上させるのに有効であり、Ｃｒを少な
くとも２％超添加させることによって、へたり特性が著
しく改善させることがわかった。即ち図１は耐へたり性
を示す残留剪断歪量とＣｒ添加量との関係を示すグラフ
であり、従来ではＣｒの添加量は１％以下であったが、
本発明で規定する様にＣｒ添加量を２％超とすることに
よって耐へたり性が著しく改善されることを見出し、本
発明を完成した。本発明に係る高強度ばね用鋼における
化学成分限定理由は下記の通りである。In order to improve the fatigue life of the spring, it is necessary to improve the toughness of the material. The present inventors selected 0.35 to 0.65% as a C range that can improve toughness while maintaining high strength. Then, when various means were investigated for improving the sag characteristic in this range, especially Cr
Was effective in improving the sag resistance, and it was found that the sag characteristic was remarkably improved by adding at least 2% of Cr. That is, FIG. 1 is a graph showing the relationship between the amount of residual shear strain showing the sag resistance and the amount of added Cr. In the conventional case, the amount of added Cr was 1% or less.
The present invention has been completed by finding that the sag resistance is remarkably improved by increasing the Cr addition amount to more than 2% as specified in the present invention. The reasons for limiting the chemical composition in the high-strength spring steel according to the present invention are as follows.
【０００８】Ｃ：0.35〜0.65％ Ｃは焼入れ焼戻し後の強度を確保するために必要な元素
である。Ｃ含有量が0.35％未満では、焼入後のマルテン
サイトの硬さが低くなり過ぎ、焼入れ焼戻し後の強度が
不足する。また0.65％を超えて過多に添加すると、焼入
れ焼戻し後の靭性が劣化し、希望する疲労特性が得られ
ない。更に、圧延時の過冷の発生を防止し、作業性を改
善すると共に、ばね製造時に表面脱炭および表面疵を除
去する為の切削や研削による素材加工が容易に行なえる
という観点からも上記範囲とする必要がある。C: 0.35 to 0.65% C is an element necessary to secure the strength after quenching and tempering. When the C content is less than 0.35%, the hardness of martensite after quenching becomes too low and the strength after quenching and tempering becomes insufficient. Further, if added in excess of 0.65%, the toughness after quenching and tempering deteriorates and desired fatigue properties cannot be obtained. Further, from the viewpoint of preventing overcooling during rolling, improving workability, and easily performing material processing by cutting or grinding to remove surface decarburization and surface defects during spring production, Must be in range.
【０００９】Ｓｉ：１〜３％ Ｓｉは固溶強化元素として必要であり、１％未満ではマ
トリックス強度が十分に得られない。しかしながら３％
を超えて添加すると、熱処理時に炭化物の溶け込みが不
十分になって、ばねにおける耐へたり性が劣化するばか
りか、内部酸化が進行してばねとして有害である脱炭を
生じさせる。 Ｍｎ：0.5 〜２％ Ｍｎが0.5 未満では、伸線性に悪影響を及ぼすＳを固定
するのに不十分であり、0.5 ％以上は必要である。また
上限を２％としたのは、耐へたり性に対して有害な残留
オーステナイト量を抑制するためである。Si: 1-3% Si is necessary as a solid solution strengthening element, and if it is less than 1%, sufficient matrix strength cannot be obtained. However 3%
If it is added in excess, the dissolution of carbide during heat treatment will be insufficient, and not only the sag resistance of the spring will deteriorate, but also internal oxidation will proceed to cause decarburization, which is harmful to the spring. Mn: 0.5 to 2% If Mn is less than 0.5, it is insufficient to fix S that adversely affects the wire drawability, and 0.5% or more is necessary. Further, the upper limit is set to 2% in order to suppress the amount of retained austenite which is harmful to the sag resistance.
【００１０】Ｎｉ：４％以下 Ｎｉは焼入れ焼戻し後の素材靭性を向上させる元素であ
るが、高価な元素であるため経済性を考慮して４％以下
とした。 Ｃｒ：２超〜３％ Ｃｒの添加はばね特性として重要な耐へたり特性を大幅
に改善することが種々の検討から明らかになった。２％
以下では高締め付加において十分な耐へたり性が得られ
ないことから、Ｃｒは少なくとも２％超を添加する必要
がある。またＣｒは焼入性向上に有効であり、耐熱性を
改善する元素でもある。しかしながらあまり多く添加し
すぎると焼入れ焼戻し処理時の加熱で未溶解炭化物が多
く発生するので上限は３％とすべきである。Ni: 4% or less Ni is an element that improves the material toughness after quenching and tempering, but since it is an expensive element, it was set to 4% or less in consideration of economic efficiency. Cr: more than 2% to 3% It has become clear from various studies that the addition of Cr significantly improves the sag resistance, which is important as spring characteristics. 2%
In the following, it is necessary to add at least more than 2% of Cr, because sufficient sag resistance cannot be obtained in addition of high tightening. Further, Cr is effective for improving hardenability and is also an element for improving heat resistance. However, if too much is added, a large amount of undissolved carbide is generated by heating during quenching and tempering treatment, so the upper limit should be 3%.
【００１１】Ｍｏ：0.05〜２％ Ｍｏは炭化物生成元素であり、焼戻し時に微細な合金炭
化物を析出させ、２次硬化を促進させることによって耐
へたり性および耐疲労性を向上させる。0.05％未満では
その効果が不十分であり、１％を超えても効果が飽和す
る。 Ｖ：0.05〜0.5 ％ Ｖは結晶粒度を微細化して耐力比を高め、耐へたり性を
改善するのに有効である。この結果を有効に発揮するに
は0.05％以上の添加が必要である。しかしながら0.5 ％
を超えて添加すると、焼入れ加熱時にオーステナイト中
に固溶されない合金炭化物量が増大し、大きな塊状物と
なって残存することから疲労寿命を低下させる。Mo: 0.05 to 2% Mo is a carbide-forming element, which precipitates fine alloy carbides during tempering and promotes secondary hardening to improve sag resistance and fatigue resistance. If it is less than 0.05%, the effect is insufficient, and if it exceeds 1%, the effect is saturated. V: 0.05 to 0.5% V is effective for refining the crystal grain size to increase the yield strength ratio and improving the sag resistance. In order to exert this result effectively, it is necessary to add 0.05% or more. However, 0.5%
If added in excess, the amount of alloy carbide that is not dissolved in austenite during quenching and heating increases and remains as a large lump, which reduces the fatigue life.
【００１２】本発明の高強度ばね用鋼は、以上の元素を
基本成分とし、残部鉄および不可避不純物からなるもの
であるが、必要に応じてＮｂ，Ｔｉ，Ａｌ，Ｂ，Ｗ，Ｃ
ｕ等を含有してもよい。これらの元素を添加するときの
含有量は下記の通りである。The high-strength spring steel of the present invention contains the above elements as basic components and the balance iron and unavoidable impurities. If necessary, Nb, Ti, Al, B, W and C may be used.
You may contain u etc. The contents when these elements are added are as follows.
【００１３】Ｎｂ：0.01〜0.1 ％，Ｔｉ：0.01〜0.1 ％ ＮｂおよびＴｉはＶと同様に結晶粒度を微細化して耐力
比を高め、耐へたり性を改善するのに有効である。この
効果を有効に発揮させるには、夫々0.01％以上の添加が
必要であるが、0.1 ％を超えて過多に添加しても効果が
飽和すると共に、経済的にも不利である。 Ａｌ：0.01〜0.1 ％ Ａｌは脱酸を容易にする元素であり、0.01％以上の添加
でその効果が発揮される。しかしながら0.1 ％を超えて
添加しても、Ａｌ2 Ｏ3 の粗大介在物を生成して耐疲労
特性を低下させる。Nb: 0.01 to 0.1%, Ti: 0.01 to 0.1% Similar to V, Nb and Ti are effective in refining the grain size to increase the yield ratio and improve the sag resistance. In order to exert this effect effectively, it is necessary to add each of them by 0.01% or more. However, even if added in excess of 0.1%, the effect is saturated and it is economically disadvantageous. Al: 0.01 to 0.1% Al is an element that facilitates deoxidation, and its effect is exhibited by adding 0.01% or more. However, even if added in excess of 0.1%, coarse inclusions of Al 2 O 3 are formed and the fatigue resistance is degraded.
【００１４】Ｂ：0.0005〜0.01％ Ｂは焼入れ性および高強度を得るために有効な元素であ
り、その効果を有効に発揮させるには0.0005％以上の添
加が必要である。しかしながら0.01％を超えて添加して
も、効果が飽和すると共に、経済的にも不利である。 Ｗ：0.05〜１％ Ｗは鋼中で炭化物を形成し、焼戻し時に析出することに
より、微細析出強化を付与する元素であり、添加量が0.
05％未満では析出量が不足し、また１％を超えて添加し
ても効果が飽和する。 Ｃｕ：0.1 〜１％ Ｃｕは脱炭および耐食性改善に有効な元素であり、0.1
％未満では上記効果が発揮されない。しかしながら１％
を超えると粒界にＣｕが濃化して熱間加工時に粒界割れ
を起こすことがある。B: 0.0005 to 0.01% B is an element effective for obtaining hardenability and high strength, and 0.0005% or more must be added to bring out the effect effectively. However, even if added over 0.01%, the effect is saturated and it is economically disadvantageous. W: 0.05 to 1% W is an element which forms a carbide in steel and gives fine precipitation strengthening by precipitating during tempering.
If it is less than 05%, the amount of precipitation will be insufficient, and if it is added in excess of 1%, the effect will be saturated. Cu: 0.1 to 1% Cu is an element effective in decarburization and improving corrosion resistance, and 0.1
If it is less than%, the above effect is not exhibited. However, 1%
If it exceeds, the Cu may be concentrated in the grain boundaries, causing grain boundary cracking during hot working.
【００１５】以下本発明を実施例によって更に詳細に説
明するが、下記実施例は本発明を限定する性質のもので
はなく、前・後記の趣旨に徴して設計変更することはい
ずれも本発明の技術的範囲に含まれるものである。The present invention will be described in more detail with reference to the following examples, but the following examples are not intended to limit the present invention, and any modification of the design of the present invention can be made without departing from the spirit of the preceding and the following. It is included in the technical scope.
【００１６】[0016]
【実施例】表１に示す化学成分の発明鋼Ａ〜Ｎおよび既
存鋼を溶製した後、鍛造で115mmの角ビレットを製作
し、線材圧延によって11mmφの線材まで圧延した。得ら
れた圧延線材に対して、下記(1) または(2)の工程によ
ってばねを製造した。 (1) 熱処理→ばね成形→焼入れ焼戻し→セッチング→シ
ョットピーニング（熱間成形ばね） (2) オイルテンパー処理→ばね成形→セッチング→ショ
ットピーニング（冷間成形ばね）EXAMPLE Inventive steels A to N having the chemical composition shown in Table 1 and existing steels were melted, and then forged to manufacture a square billet of 115 mm, and rolled by wire rod to a wire rod of 11 mmφ. A spring was manufactured from the obtained rolled wire by the following process (1) or (2). (1) Heat treatment → Spring forming → Quenching and tempering → Setting → Shot peening (hot forming spring) (2) Oil temper treatment → Spring forming → Setting → Shot peening (cold forming spring)
【００１７】[0017]
【表１】 [Table 1]
【００１８】得られたばねから引張り試験片、残留剪断
歪量試験片および大気耐久限度測定試験片を準備し、夫
々の試験に供した。残留剪断測定試験および耐久限度測
定試験における条件は下記の通りである。 (1) 残留剪断測定試験（耐へたり性） （ばね緒元） 材料の線径 ：9.0 mm コイル平均径：85 mm 総巻き数 ：７巻 有効巻き数 ：5.5 巻 自由高さ ：320 mm （セッチング応力） 最大剪断応力＋10kgf/mm2 （試験条件） 締め付け応力：130kgf/mm2 試験温度 ：80℃ 試験時間 ：72時間 （残留剪断歪の算出方法） τΔｐ＝８ＤΔｐ／πｄ3 (2) τ＝Ｇγ (3) (2) ，(3) 式より γΔｐ＝τΔｐ／Ｇ×100 （％） 但し、τΔｐ：荷重損失量に相当するねじり応力(kgf/m
m2） ｄ ：線径(mm) Ｄ ：コイル平均径 Δｐ：荷重損失量 Ｇ ：横弾性係数(kgf/mm2）（8000kgf/mm2 を採用）Tensile test pieces, residual shear strain amount test pieces and atmospheric endurance limit measurement test pieces were prepared from the obtained springs and subjected to respective tests. The conditions in the residual shear measurement test and the durability limit measurement test are as follows. (1) Residual shear measurement test (sag resistance) (Spring root) Material wire diameter: 9.0 mm Coil average diameter: 85 mm Total number of windings: 7 effective windings: 5.5 free height: 320 mm ( Setting stress) Maximum shear stress + 10kgf / mm 2 (Test condition) Tightening stress: 130kgf / mm 2 Test temperature: 80 ℃ Test time: 72 hours (Calculation method of residual shear strain) τΔp = 8DΔp / πd 3 (2) τ = Gγ (3) From equations (2) and (3), γΔp = τΔp / G × 100 (%) where τΔp: torsional stress equivalent to the load loss (kgf / m
m 2 ) d: Wire diameter (mm) D: Coil average diameter Δp: Load loss amount G: Transverse elastic modulus (kgf / mm 2 ) (8000kgf / mm 2 is adopted)
【００１９】(2) 耐久限度試験 （試験条件） 試験温度：室温 時間寿命：２０万回をクリアー 表面状態：ショットピーニング肌 （疲労限の判定） ２０万回を２度クリヤーしたときの試験応力 引張り試験結果を、ばね成形法とともに表２に示す。ま
た耐へたり性を表わす残留剪断歪量と、疲労特性を表わ
す大気耐久限度応力値を表３に示す。これらの結果から
明らかであるが、本発明鋼は、強度、耐へたり性および
疲労寿命のいずれも優れた特性を示していることがよく
わかる。(2) Endurance limit test (test conditions) Test temperature: room temperature Time life: 200,000 times cleared Surface condition: shot peened skin (judgement of fatigue limit) Test stress when 200,000 times is cleared twice The test results are shown in Table 2 together with the spring forming method. Table 3 shows the residual shear strain amount indicating the sag resistance and the atmospheric endurance limit stress value indicating the fatigue property. As is clear from these results, it is clear that the steel of the present invention exhibits excellent properties in strength, fatigue resistance and fatigue life.
【００２０】[0020]
【表２】 [Table 2]
【００２１】[0021]
【表３】 [Table 3]
【００２２】[0022]
【発明の効果】以上述べた如く本発明によれば、強度が
200kgf/mm2以上であり、しかも疲労特性およびへたり特
性が良好な高強度ばねを製造する方法、およびその様な
高強度ばねを得る為の最適なばね用鋼が実現できた。As described above, according to the present invention, the strength is
It has been possible to realize a method for producing a high-strength spring having a fatigue strength and a sag characteristic of 200 kgf / mm 2 or more, and an optimum spring steel for obtaining such a high-strength spring.
【図１】残留剪断歪量とＣｒ添加量の関係を示すグラフ
である。FIG. 1 is a graph showing the relationship between the residual shear strain amount and the Cr addition amount.
Claims (8)
同じ），Ｓｉ：１〜３％，Ｍｎ：0.5 〜２％，Ｎｉ：４
％以下，Ｃｒ：２超〜３％，Ｍｏ：0.05〜１％，Ｖ：0.
05〜0.5 ％を夫々含有し、残部鉄および不可避不純物か
らなることを特徴とする高強度ばね用鋼。1. C: 0.35 to 0.65% (meaning weight%; the same applies hereinafter), Si: 1 to 3%, Mn: 0.5 to 2%, Ni: 4
% Or less, Cr: over 2 to 3%, Mo: 0.05 to 1%, V: 0.
High-strength spring steel characterized by containing 05-0.5% of each and the balance iron and unavoidable impurities.
て、更にＮｂ：0.01〜0.1 ％およびＴｉ：0.01〜0.1 ％
から選ばれる１種または２種を含有するものである高強
度ばね用鋼。2. The high strength spring steel according to claim 1, further comprising Nb: 0.01 to 0.1% and Ti: 0.01 to 0.1%.
A high-strength spring steel containing one or two selected from the following.
鋼において、更にＡｌ：0.01〜0.1 ％を含有するもので
ある高強度ばね用鋼。3. The high-strength spring steel according to claim 1 or 2, further comprising Al: 0.01 to 0.1%.
ばね用鋼において、更にＢ：0.0005〜0.01％を含有する
ものである高強度ばね用鋼。4. The high strength spring steel according to claim 1, further comprising B: 0.0005 to 0.01%.
ばね用鋼において、更にＷ：0.05〜１％を含有するもの
である高強度ばね用鋼。5. The high-strength spring steel according to claim 1, further containing W: 0.05 to 1%.
ばね用鋼において、更にＣｕ：0.1 〜１％を含有するも
のである高強度ばね用鋼。6. The high-strength spring steel according to any one of claims 1 to 5, further containing Cu: 0.1 to 1%.
鋼を用い、熱間ばね成形後焼入れ焼戻し処理を施し、更
にセッチングおよびショットピーニングを施して高強度
を得ることを特徴とする高強度ばねの製造方法。7. The spring steel according to any one of claims 1 to 6 is characterized in that high strength is obtained by performing quenching and tempering treatment after hot spring forming, and further setting and shot peening. Method for manufacturing high strength spring.
鋼を用い、オイルテンパー処理を施して高強度を得た
後、冷間ばね成形し、更にセッチンクおよびショットピ
ーニングすることを特徴とする高強度ばねの製造方法。8. The spring steel according to claim 1, which is subjected to oil temper treatment to obtain high strength, cold spring formed, and further settling and shot peening. And a method for manufacturing a high strength spring.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP34001291A JPH05148581A (en) | 1991-11-28 | 1991-11-28 | Steel for high strength spring and production thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP34001291A JPH05148581A (en) | 1991-11-28 | 1991-11-28 | Steel for high strength spring and production thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH05148581A true JPH05148581A (en) | 1993-06-15 |
Family
ID=18332906
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP34001291A Pending JPH05148581A (en) | 1991-11-28 | 1991-11-28 | Steel for high strength spring and production thereof |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH05148581A (en) |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR101219837B1 (en) * | 2010-10-19 | 2013-01-08 | 기아자동차주식회사 | Method for manufacturing of high strength valve spring for vehicle engine and high strength valve spring using the same |
| JP2014509348A (en) * | 2011-01-28 | 2014-04-17 | シーアールエス ホールディングス，インコーポレイテッド | High strength and high toughness steel alloy |
| CN106086651A (en) * | 2016-08-03 | 2016-11-09 | 苏州市虎丘区浒墅关弹簧厂 | A kind of spring high-ductility alloy material |
| US10487381B2 (en) | 2016-06-21 | 2019-11-26 | Hyundai Motor Company | Ultrahigh-strength spring steel |
| US10494705B2 (en) | 2015-12-04 | 2019-12-03 | Hyundai Motor Company | Ultra high-strength spring steel |
| US10689736B2 (en) | 2015-12-07 | 2020-06-23 | Hyundai Motor Company | Ultra-high-strength spring steel for valve spring |
| US10718039B2 (en) | 2016-04-15 | 2020-07-21 | Hyundai Motor Company | High strength spring steel having excellent corrosion resistance |
| CN114959486A (en) * | 2022-06-13 | 2022-08-30 | 杭州兴发弹簧有限公司 | 42SiCrV6 spring steel for large-wire-diameter hot-rolling spring on large excavator |
-
1991
- 1991-11-28 JP JP34001291A patent/JPH05148581A/en active Pending
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR101219837B1 (en) * | 2010-10-19 | 2013-01-08 | 기아자동차주식회사 | Method for manufacturing of high strength valve spring for vehicle engine and high strength valve spring using the same |
| US8470104B2 (en) | 2010-10-19 | 2013-06-25 | Hyundai Motor Company | High strength valve spring for vehicle engine and method of manufacturing the same |
| JP2014509348A (en) * | 2011-01-28 | 2014-04-17 | シーアールエス ホールディングス，インコーポレイテッド | High strength and high toughness steel alloy |
| US10494705B2 (en) | 2015-12-04 | 2019-12-03 | Hyundai Motor Company | Ultra high-strength spring steel |
| US10689736B2 (en) | 2015-12-07 | 2020-06-23 | Hyundai Motor Company | Ultra-high-strength spring steel for valve spring |
| US10718039B2 (en) | 2016-04-15 | 2020-07-21 | Hyundai Motor Company | High strength spring steel having excellent corrosion resistance |
| US10487381B2 (en) | 2016-06-21 | 2019-11-26 | Hyundai Motor Company | Ultrahigh-strength spring steel |
| CN106086651A (en) * | 2016-08-03 | 2016-11-09 | 苏州市虎丘区浒墅关弹簧厂 | A kind of spring high-ductility alloy material |
| CN114959486A (en) * | 2022-06-13 | 2022-08-30 | 杭州兴发弹簧有限公司 | 42SiCrV6 spring steel for large-wire-diameter hot-rolling spring on large excavator |
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