JP4302480B2 - High hardness steel with excellent cold workability - Google Patents
High hardness steel with excellent cold workability Download PDFInfo
- Publication number
- JP4302480B2 JP4302480B2 JP2003359577A JP2003359577A JP4302480B2 JP 4302480 B2 JP4302480 B2 JP 4302480B2 JP 2003359577 A JP2003359577 A JP 2003359577A JP 2003359577 A JP2003359577 A JP 2003359577A JP 4302480 B2 JP4302480 B2 JP 4302480B2
- Authority
- JP
- Japan
- Prior art keywords
- less
- hardness
- cold
- annealing
- high hardness
- 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
- 229910000831 Steel Inorganic materials 0.000 title claims description 11
- 239000010959 steel Substances 0.000 title claims description 11
- 238000000137 annealing Methods 0.000 claims description 16
- 229910052758 niobium Inorganic materials 0.000 claims description 6
- 229910052804 chromium Inorganic materials 0.000 claims description 5
- 229910052750 molybdenum Inorganic materials 0.000 claims description 5
- 239000012535 impurity Substances 0.000 claims description 4
- 229910052748 manganese Inorganic materials 0.000 claims description 4
- 229910052720 vanadium Inorganic materials 0.000 claims description 4
- 238000005496 tempering Methods 0.000 description 15
- 230000000694 effects Effects 0.000 description 11
- 239000000463 material Substances 0.000 description 9
- 230000000052 comparative effect Effects 0.000 description 8
- 230000007797 corrosion Effects 0.000 description 7
- 238000005260 corrosion Methods 0.000 description 7
- 150000001247 metal acetylides Chemical class 0.000 description 7
- 238000010791 quenching Methods 0.000 description 7
- 230000000171 quenching effect Effects 0.000 description 7
- 238000010438 heat treatment Methods 0.000 description 6
- 239000000523 sample Substances 0.000 description 6
- 230000007423 decrease Effects 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 229910052721 tungsten Inorganic materials 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 229910000967 As alloy Inorganic materials 0.000 description 1
- 229910000822 Cold-work tool steel Inorganic materials 0.000 description 1
- 229910000746 Structural steel Inorganic materials 0.000 description 1
- 229910001315 Tool steel Inorganic materials 0.000 description 1
- 229910000870 Weathering steel Inorganic materials 0.000 description 1
- 230000001133 acceleration Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000010622 cold drawing Methods 0.000 description 1
- 238000010273 cold forging Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 238000007542 hardness measurement Methods 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 238000004381 surface treatment Methods 0.000 description 1
- 238000009736 wetting Methods 0.000 description 1
Landscapes
- Heat Treatment Of Articles (AREA)
Description
本発明は、冷間加工により製造される部品に適した高硬度鋼に関するものである。 The present invention relates to a high hardness steel suitable for parts manufactured by cold working.
従来、自動車、精密機械、ＯＡ機器などの高硬度が必要な部品には、構造用鋼に表面処理を施して使用する場合が多い。しかし、耐候性、耐摩耗性が必要な場合には、ＪＩＳ−ＳＫＤ１１、ＳＵＪ２などの高硬度鋼を使用し、冷間鍛造などの冷間加工により製造させる場合が多い。このように、ＳＵＪ２の耐摩耗性、耐候性が不十分な場合には、ＳＫＤ１１が用いられるが、ＳＫＤ１１は冷間加工性が悪く、また、焼入焼戻し時の硬さも６０ＨＲＣ程度しか得られないことから、冷間加工性に優れ、焼入焼戻し時に高硬度が得られる材料が望まれている。 Conventionally, structural steel is often subjected to surface treatment for parts that require high hardness, such as automobiles, precision machines, and OA equipment. However, when weather resistance and wear resistance are required, high-hardness steels such as JIS-SKD11 and SUJ2 are often used and manufactured by cold working such as cold forging. Thus, when the wear resistance and weather resistance of SUJ2 are insufficient, SKD11 is used. However, SKD11 has poor cold workability, and the hardness at the time of quenching and tempering can be obtained only about 60 HRC. Therefore, a material that is excellent in cold workability and that can obtain high hardness during quenching and tempering is desired.
この冷間加工性が良く、比較的耐食性に優れ、焼入焼戻しにより５８ＨＲＣ以上の硬さが得られる高硬度耐候性鋼として、例えば特開平４−３６２１５３号公報（特許文献１）に開示されているように、合金成分として、Ｃ：０．４５〜０．６５％、Ｓｉ：０．２５％以下、Ｍｎ：０．２５％以下、Ｎｉ：０．６％以下、Ｃｒ：４．０〜１１．０％、Ｍｏ：０．２〜１．０％、Ａｌ：０．０３％以下およびＣａ：０．００１〜０．０２０％を含有し、不純物を、Ｐ：０．０３％以下、Ｓ：０．００５％以下、Ｏ：０．００５％以下に規制し、残部が実質的にＦｅからなる鋼が提案されている。 As this high-hardness weathering steel having good cold workability, relatively excellent corrosion resistance, and hardness of 58 HRC or more obtained by quenching and tempering, it is disclosed in, for example, Japanese Patent Laid-Open No. 4-362153 (Patent Document 1). As described above, as alloy components, C: 0.45-0.65%, Si: 0.25% or less, Mn: 0.25% or less, Ni: 0.6% or less, Cr: 4.0-11 0.0%, Mo: 0.2-1.0%, Al: 0.03% or less and Ca: 0.001-0.020%, impurities: P: 0.03% or less, S: There has been proposed a steel which is limited to 0.005% or less and O: 0.005% or less, and the balance is substantially made of Fe.
また、金型寿命に優れた冷間工具鋼として、特開平１１−１９３４４７号公報（特許文献２）に開示されている。これは合金成分として、重量％で、Ｃ：０．６５〜１．３％、Ｓｉ：２．０％以下、Ｍｎ：０．１〜２．０％、Ｃｒ：５．０〜１１．０％、ＭｏまたはＷのいずれか１種または２種をＭｏ当量（Ｍｏ＋１／２Ｗ）：０．７〜５．０％、ＶまたはＮｂのいずれか１種または２種をＶ当量（Ｖ＋１／２Ｎｂ）：０．１〜２．５％残部Ｆｅおよび不可避的不純物よりなり、Ｍ7 Ｃ3 型炭化物の粒径を５〜１５μｍ、面積率１〜９％とすることにより耐疲労強度の優れた型寿命を有することを特徴とする冷間工具鋼にある。 Moreover, it is disclosed by Unexamined-Japanese-Patent No. 11-193447 (patent document 2) as cold tool steel excellent in the metal mold | die lifetime. This is an alloy component in weight%, C: 0.65-1.3%, Si: 2.0% or less, Mn: 0.1-2.0%, Cr: 5.0-11.0% Any one or two of Mo or W is equivalent to Mo (Mo + 1 / 2W): 0.7 to 5.0%, and any one or two of V or Nb is equivalent to V (V + 1 / 2Nb): It consists of 0.1 to 2.5% balance Fe and inevitable impurities, and the M 7 C 3 type carbide has a particle size of 5 to 15 μm and an area ratio of 1 to 9%, thereby providing a mold life with excellent fatigue strength. It is in the cold work tool steel characterized by having.
しかしながら、上述した特許文献１は、低温焼戻しでしか高硬度が得られないため、使用中温度が上昇する部品には適用できない。また、硬質炭化物が少ない成分系であり、焼入焼戻硬さおよび耐摩耗性の点で不十分である。また、特許文献２は、金型に用いるものであり、本発明が課題とした被加工材として部品に用いられる場合は全く想定しておらず、冷間加工性の点で不十分である。 However, Patent Document 1 described above cannot be applied to a component whose temperature rises during use because high hardness can be obtained only by low-temperature tempering. Moreover, it is a component system with few hard carbides, and is insufficient in terms of quenching and tempering hardness and wear resistance. Further, Patent Document 2 is used for a mold, and is not assumed at all when it is used for a part as a material to be processed, which is a problem to be solved by the present invention, and is insufficient in terms of cold workability.
上述したような問題を解消するために、発明者らは鋭意開発を進めた結果、耐候性と冷間加工性に優れ、かつ使用中温度が上昇する部品への適用を考慮し、低温および高温焼戻しの広範囲の熱処理により５８〜６３ＨＲＣの高硬度が得られる鋼を提供するものである。その発明の要旨とするところは、
（１）質量％で、Ｃ：０．６５〜１．１％、Ｓｉ：０．１〜１．５％、Ｍｎ：０．１〜１．０％、Ｃｒ：５．０〜１１．０％、ＭｏまたはＷのいずれか１種または２種をＭｏ当量（Ｍｏ＋１／２Ｗ）：０．５〜２．０％、ＶまたはＮｂのいずれか１種または２種をＶ当量（Ｖ＋１／２Ｎｂ）：０．１〜１．５％、Ｏ：３０ｐｐｍ以下、Ｎ：０．０５％以下、Ｓ：０．００５％以下、残部Ｆｅおよび不可避的不純物よりなる鋼を焼鈍した後の炭化物粒度を２０μｍ以下に微細化し、冷鍛性の向上を図ると共に、焼鈍硬さ９８ＨＲＢ以下としたことを特徴とする冷間加工性に優れた高硬度鋼にある。
In order to solve the above-mentioned problems, the inventors have intensively developed, and as a result, considering the application to parts that have excellent weather resistance and cold workability and the temperature during use increases, The present invention provides a steel having a high hardness of 58 to 63 HRC by a wide range of tempering heat treatments. The gist of the invention is that
(1) By mass%, C: 0.65-1.1%, Si: 0.1-1.5%, Mn: 0.1-1.0%, Cr: 5.0-11.0% Any one or two of Mo or W is equivalent to Mo (Mo + 1 / 2W): 0.5 to 2.0 %, and one or two of V or Nb is equivalent to V (V + 1 / 2Nb): 0.1 to 1.5%, O: 30 ppm or less, N: 0.05% or less, S: 0.005% or less, Carbide particle size after annealing steel consisting of the remainder Fe and inevitable impurities to 20 μm or less It is a high-hardness steel excellent in cold workability, characterized by being refined and improving cold forgeability, and having an annealing hardness of 98 HRB or less .
本発明により、耐候性と冷間加工性に優れ、かつ使用中温度が上昇する部品への適用を考慮し、低温および高温焼戻しの広範囲の熱処理により５８〜６３ＨＲＣの高硬度が得られる鋼が得られる極めて優れた効果を奏するものである。 According to the present invention, in consideration of application to parts that are excellent in weather resistance and cold workability and whose temperature increases during use, a steel having a high hardness of 58 to 63 HRC can be obtained by a wide range of low temperature and high temperature tempering heat treatments. It has an extremely excellent effect.
以下、本発明に係る成分組成の限定理由を説明する。
Ｃ：０．６５〜１．１％
Ｃは、焼入焼戻し時のマトリックス硬さ、炭化物形成のため必要な元素であり、合金元素と結合して硬質炭化物を形成し耐摩耗性を向上させる。しかし、０．６５％未満ではその効果が十分でなく、１．１％を超える添加は、Ｃｒと結合して粗大炭化物を形成し、冷鍛性を低下させると共に、焼鈍硬さを高め、冷鍛性を低下させる。従って、その範囲を０．６５〜１．１％とした。望ましくは０．７５〜０．９５％とする。
Hereinafter, the reasons for limiting the component composition according to the present invention will be described.
C: 0.65-1.1%
C is an element necessary for matrix hardness and carbide formation during quenching and tempering, and combines with alloy elements to form hard carbide and improve wear resistance. However, if the content is less than 0.65%, the effect is not sufficient. Addition exceeding 1.1% combines with Cr to form coarse carbides, lowers the cold forgeability, increases the annealing hardness, Reduces forgeability. Therefore, the range was made 0.65-1.1%. Desirably, the content is 0.75 to 0.95%.
Ｓｉ：０．１〜１．５％
Ｓｉは、脱酸剤、耐酸化性、焼入性、二次硬化促進、および耐候性を付与させる元素である。しかし、０．１％未満ではその効果は十分でなく、１．５％を超えると焼鈍硬さを高め、冷鍛性を低下させる。従って、その範囲を０．１〜１．５％とした。望ましくは０．６〜１．２％とする。
Ｍｎ：０．１〜１．０％
Ｍｎは、脱酸剤、および焼入性を付与させる元素である。しかし、０．１％未満ではその効果は十分でなく、１．０％を超えると介在物を形成し、冷鍛性を低下させる。従って、その範囲を０．１〜１．０％とした。
Si: 0.1 to 1.5%
Si is an element that imparts a deoxidizer, oxidation resistance, hardenability, secondary curing acceleration, and weather resistance. However, if it is less than 0.1%, the effect is not sufficient, and if it exceeds 1.5%, the annealing hardness is increased and the cold forgeability is lowered. Therefore, the range was made 0.1 to 1.5%. Desirably, it is 0.6 to 1.2%.
Mn: 0.1 to 1.0%
Mn is an element that imparts a deoxidizing agent and hardenability. However, if it is less than 0.1%, the effect is not sufficient, and if it exceeds 1.0%, inclusions are formed and cold forgeability is lowered. Therefore, the range was made 0.1 to 1.0%.
Ｃｒ：５．０〜１１．０％
Ｃｒは、焼入性、耐軟化抵抗性、炭化物を形成し耐摩耗性向上および耐食性（耐候性）を向上させる元素である。しかし、５．０％未満ではその効果は十分でなく、１１．０％を超えるとＣと結合して粗大炭化物を形成し、冷鍛性を低下させる。従って、その範囲を５．０〜１１．０％とした。望ましくは７．０〜９．０％とする。
Cr: 5.0 to 11.0%
Cr is an element that forms hardenability, resistance to softening, and forms carbides to improve wear resistance and corrosion resistance (weather resistance). However, if it is less than 5.0%, the effect is not sufficient, and if it exceeds 11.0%, it combines with C to form coarse carbides and lowers cold forgeability. Therefore, the range was made 5.0 to 11.0%. Desirably, it is 7.0 to 9.0%.
（Ｍｏ＋１／２Ｗ）：０．５〜２．０％
ＭｏおよびＷは、共に微細な炭化物を形成し、二次硬化に寄与する重要な元素である。ただし、その効果はＭｏの方がＷよりも２倍強く、同じ効果を得るのに、ＷはＭｏの２倍必要である。この両元素の効果は、Ｍｏ当量（Ｍｏ＋１／２Ｗ）で表すことができる。本発明成分系においては、Ｍｏ当量で０．５％以上必要である。逆に、Ｍｏ当量が２．０％を超えると焼鈍硬さを高め、冷鍛性を低下させることから、その上限を２．０％とした。
(Mo + 1 / 2W): 0.5-2.0 %
Mo and W are both important elements that form fine carbides and contribute to secondary hardening. However, the effect of Mo is twice as strong as that of W. To obtain the same effect, W needs to be twice that of Mo. The effect of both elements can be expressed by Mo equivalent (Mo + 1 / 2W). In the component system of the present invention, the Mo equivalent is 0.5% or more. Conversely, if the Mo equivalent exceeds 2.0 %, the annealing hardness is increased and the cold forgeability is lowered, so the upper limit was made 2.0 % .
Ｖ当量（Ｖ＋１／２Ｎｂ）：０．１〜１．５％
Ｖ、Ｎｂは、共に二次硬化に有効であり、Ｃと硬い炭化物を形成して耐摩耗性の向上に大きく寄与すると共に結晶粒を微細化する。ただし、その効果はＶの方がＮｂよりも２倍強く、同じ効果を得るのに、ＮｂはＶの２倍必要である。この両元素の効果はＶ当量（Ｖ＋１／２Ｎｂ）で表すことができる。本発明成分系においては、高温焼戻し硬度を得るためには、Ｖ当量で０．１％以上必要である。逆に、Ｍｏ当量が１．５％を超えると焼鈍硬さを高め、冷鍛性を低下させることから、その上限を１．５％とした。望ましくは０．３〜１．０とする。
V equivalent (V + 1 / 2Nb): 0.1 to 1.5%
V and Nb are both effective for secondary curing, and form a hard carbide with C to greatly contribute to the improvement of wear resistance and to refine crystal grains. However, the effect of V is twice as strong as that of Nb, and Nb needs to be twice that of V to obtain the same effect. The effect of both elements can be expressed in terms of V equivalent (V + 1 / 2Nb). In the component system of the present invention, in order to obtain high temperature tempering hardness, 0.1% or more in V equivalent is necessary. Conversely, if the Mo equivalent exceeds 1.5%, the annealing hardness is increased and the cold forgeability is lowered, so the upper limit was made 1.5%. Desirably 0.3 to 1.0.
Ｏ：３０ｐｐｍ以下
Ｏは、冷間鍛造性を低下させるので、その上限を３０ｐｐｍとする。なお、望ましくは１５ｐｐｍ以下である。
Ｎ：０．０５％以下
Ｎは、冷間鍛造性を低下させるので、その上限を０．０５％とする。なお、望ましくは０．０３％以下である。
Ｓ：０．００５％以下
Ｓは、冷間鍛造性を低下させるので、その上限を０．００５％とする。なお、望ましくは０．００３％以下である。
O: 30 ppm or less O lowers the cold forgeability, so the upper limit is made 30 ppm. In addition, it is 15 ppm or less desirably.
N: 0.05% or less N lowers the cold forgeability, so the upper limit is made 0.05%. Desirably, it is 0.03% or less.
S: 0.005% or less S lowers the cold forgeability, so the upper limit is made 0.005%. Desirably, it is 0.003% or less.
焼鈍硬さ９８ＨＲＢ以下
焼鈍硬さは、９８ＨＲＢを超えると冷鍛性を低下させる。従って、その上限を９８ＨＲＢとする。望ましくは９６ＨＲＢとする。
炭化物粒度を２０μｍ以下
焼鈍後の炭化物の粒度は、２０μｍを超えると冷鍛性を低下させる。従って、その上限を２０μｍとする。
Annealing hardness 98HRB or less When the annealing hardness exceeds 98HRB, the cold forgeability is lowered. Therefore, the upper limit is set to 98 HRB. Desirably 96HRB.
When the particle size of the carbide after annealing is 20 μm or less, the cold forgeability is deteriorated. Therefore, the upper limit is 20 μm.
以下に、本発明を実施例に基づいて具体的に説明する。
表１に示す成分組成の鋼１００ｋｇを真空誘導溶解炉にて出鋼した後、インゴットに鋳造し、１１００℃に加熱し、φ３０に鍛伸を行い供試材とした。この試験片を、７００〜９５０℃で保持後徐冷する焼鈍処理を１回以上行い、必要に応じて、冷間引抜き、７００〜９５０℃で保持後徐冷する焼鈍処理を１回以上行なった。その結果を表２に示す。
The present invention will be specifically described below based on examples.
After 100 kg of steel having the component composition shown in Table 1 was produced in a vacuum induction melting furnace, it was cast into an ingot, heated to 1100 ° C., forged to φ30, and used as a test material. This test piece was annealed at least once after being held at 700 to 950 ° C. and then annealed once or more, if necessary, by cold drawing and annealing at a temperature of 700 to 950 ° C. after annealing. . The results are shown in Table 2.
表２に示す冷間加工性試験は、焼鈍状態、φ１４×２１Ｌに加工後、冷間据込み試験を行う。また、焼入焼戻し硬さ測定は、焼入れ１０３０℃、空冷、焼戻し１００〜６００℃の各温度、空冷を２回行なった。また、耐摩耗性試験は、大越式摩耗試験機を用い、ＳＮＣＭ製リングを押しつけることにより摩耗量を評価した。その評価は、○：耐摩耗性良好、△：耐摩耗性やや劣る。×：耐摩耗性に劣る。××：耐摩耗性が極めて悪い、４段階とした。さらに、耐食性試験は、湿潤（４０℃、９８％ＲＨ、４時間）→乾燥（２時間）を５サイクル繰り返し、発錆状態を評価した。その評価は、○：耐食性良好、△：耐食性不良、×：耐食性悪い、３段階とした。 The cold workability test shown in Table 2 performs a cold upsetting test after processing into an annealed state, φ14 × 21L. In addition, the quenching and tempering hardness measurement was performed twice by quenching 1030 ° C., air cooling, each temperature of tempering 100 to 600 ° C., and air cooling twice. In the wear resistance test, the wear amount was evaluated by pressing an SNCM ring using an Ogoshi type wear tester. The evaluation is: ○: good wear resistance, Δ: slightly poor wear resistance. X: Inferior in wear resistance. XX: Four stages with extremely poor wear resistance. Further, in the corrosion resistance test, wetting (40 ° C., 98% RH, 4 hours) → drying (2 hours) was repeated 5 cycles to evaluate the rusting state. The evaluation was made into three stages: ○: good corrosion resistance, Δ: poor corrosion resistance, ×: bad corrosion resistance.
表２に示すように、供試材Ａ〜Ｅは本発明例であり、供試材Ｆ〜Ｌは比較例である。比較例である供試材ＦはＣ量が少なく、かつＭｏ／Ｗの値が低いために、低温および高温焼戻しの広範囲の熱処理により高硬度が得られず、また、耐摩耗性および耐食性に劣る。比較例である供試材ＧはＣ量が多いために、供試材Ｆと同様に、低温および高温焼戻しの広範囲の熱処理により高硬度が得られず、また、耐摩耗性および焼鈍硬さを高め、冷鍛性を低下させる。 As shown in Table 2, sample materials A to E are examples of the present invention, and sample materials F to L are comparative examples. Since the test material F as a comparative example has a small amount of C and a low Mo / W value, high hardness cannot be obtained by a wide range of heat treatments at low temperature and high temperature tempering, and it is inferior in wear resistance and corrosion resistance. . Since the sample material G which is a comparative example has a large amount of C, like the sample material F , high hardness cannot be obtained by a wide range of heat treatments at low temperature and high temperature tempering, and the wear resistance and annealing hardness can be reduced. Increase and decrease cold forgeability.
比較例である供試材ＨはＣｒ量が多く、Ｃと結合して粗大炭化物を形成し、耐摩耗性および焼鈍硬さを高め、冷鍛性を低下させ、かつ、低温および高温焼戻しの広範囲の熱処理により高硬度が得られない。比較例である供試材ＩはＣ量およびＣｒ量が多いために、粗大炭化物を形成し、焼鈍硬さを高め、冷鍛性を低下させる。比較例である供試材ＪはＣ量が低く、Ｍｏ／Ｗ値が低い、かつＯ量が高いために、低温および高温焼戻しの広範囲の熱処理により高硬度が得られず、また、冷鍛性に劣る。比較例である供試材ＫはＮ量が多いために、冷鍛性に劣る。さらに、比較例である供試材ＬはＳ量が多いために、冷鍛性を低下させる。 Sample H, which is a comparative example, has a large amount of Cr, combines with C to form coarse carbides, increases wear resistance and annealing hardness, decreases cold forgeability, and has a wide range of low temperature and high temperature tempering. High hardness cannot be obtained by this heat treatment. Since the test material I which is a comparative example has a large amount of C and Cr, it forms coarse carbides, increases the annealing hardness, and decreases the cold forgeability. Since the test material J, which is a comparative example, has a low C content, a low Mo / W value, and a high O content, high hardness cannot be obtained by a wide range of low temperature and high temperature tempering heat treatments. Inferior to Since the sample material K which is a comparative example has a large amount of N, it is inferior in cold forgeability. Furthermore, since the test material L which is a comparative example has a large amount of S, the cold forgeability is lowered.
Claims (1)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2003359577A JP4302480B2 (en) | 2003-10-20 | 2003-10-20 | High hardness steel with excellent cold workability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2003359577A JP4302480B2 (en) | 2003-10-20 | 2003-10-20 | High hardness steel with excellent cold workability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2005120455A JP2005120455A (en) | 2005-05-12 |
| JP4302480B2 true JP4302480B2 (en) | 2009-07-29 |
Family
ID=34615757
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2003359577A Expired - Lifetime JP4302480B2 (en) | 2003-10-20 | 2003-10-20 | High hardness steel with excellent cold workability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP4302480B2 (en) |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2015040315A (en) * | 2013-08-20 | 2015-03-02 | 山陽特殊製鋼株式会社 | Die alloy tool steel having small anisotropy and dimensional change due to heat treatment |
| JP6177694B2 (en) * | 2014-01-06 | 2017-08-09 | 山陽特殊製鋼株式会社 | Steel for cold press dies |
| JP7062961B2 (en) | 2017-03-28 | 2022-05-09 | 大同特殊鋼株式会社 | Annealed steel and its manufacturing method |
| JP2020111766A (en) * | 2019-01-08 | 2020-07-27 | 山陽特殊製鋼株式会社 | Cold tool steel |
-
2003
- 2003-10-20 JP JP2003359577A patent/JP4302480B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JP2005120455A (en) | 2005-05-12 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP7083242B2 (en) | Hot tool steel with excellent thermal conductivity | |
| JP2020070457A (en) | Hot work tool steel having excellent thermal conductivity | |
| WO2007123164A1 (en) | Piston ring material for internal combustion engine | |
| JP2011195917A (en) | Hot work tool steel excellent in toughness | |
| CN109790602B (en) | Steel | |
| JP2021017623A (en) | Tool steel for hot work, excellent in thermal conductivity | |
| JP6620490B2 (en) | Age-hardening steel | |
| WO2018139185A1 (en) | Hot work tool steel with excellent thermal conductivity | |
| JP3954751B2 (en) | Steel with excellent forgeability and machinability | |
| JP4396561B2 (en) | Induction hardening steel | |
| JP2004238702A (en) | Carburized component excellent in low-cycle impact fatigue resistance | |
| JP4302480B2 (en) | High hardness steel with excellent cold workability | |
| JP6903507B2 (en) | Hot tool steel with excellent hardenability and toughness | |
| JP5050515B2 (en) | Non-tempered steel containing V for crankshaft | |
| JP7149250B2 (en) | Hot work tool steel with excellent high temperature strength and toughness | |
| JP7141944B2 (en) | Non-tempered forged parts and steel for non-tempered forgings | |
| JP7220750B1 (en) | Hot work tool steel with excellent high-temperature strength and toughness | |
| WO2006057470A1 (en) | Steel wire for cold forging | |
| JPH11335773A (en) | Bearing steel excellent in cold workability | |
| JP3750835B2 (en) | High hardness corrosion resistant powder die steel excellent in mirror finish and method for producing the same | |
| JP6662107B2 (en) | Non-tempered steel for hot forging and automotive parts | |
| JP2004315840A (en) | Cold working tool steel superior in machinability, and manufacturing method therefor | |
| JP2023140901A (en) | High hardness steel for cold working and machine component using the same | |
| JP3728014B2 (en) | Machine structural steel with excellent cold forgeability and induction hardenability | |
| JP2000248332A (en) | Die excellent in heat resistance, and its manufacture |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20060206 |
|
| A977 | Report on retrieval |
Free format text: JAPANESE INTERMEDIATE CODE: A971007 Effective date: 20080213 |
|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20080226 |
|
| A521 | Request for written amendment filed |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20080325 |
|
| TRDD | Decision of grant or rejection written | ||
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 Effective date: 20090421 |
|
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 |
|
| A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20090422 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20120501 Year of fee payment: 3 |
|
| R150 | Certificate of patent or registration of utility model |
Free format text: JAPANESE INTERMEDIATE CODE: R150 Ref document number: 4302480 Country of ref document: JP Free format text: JAPANESE INTERMEDIATE CODE: R150 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20130501 Year of fee payment: 4 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20130501 Year of fee payment: 4 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20140501 Year of fee payment: 5 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| EXPY | Cancellation because of completion of term |