KR101745191B1 - Ultra high strength spring steel - Google Patents
Ultra high strength spring steel Download PDFInfo
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- KR101745191B1 KR101745191B1 KR1020150171889A KR20150171889A KR101745191B1 KR 101745191 B1 KR101745191 B1 KR 101745191B1 KR 1020150171889 A KR1020150171889 A KR 1020150171889A KR 20150171889 A KR20150171889 A KR 20150171889A KR 101745191 B1 KR101745191 B1 KR 101745191B1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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Abstract
The present invention relates to an ultra-high strength spring steel which is improved in tensile strength and fatigue strength so that it can be used for an engine valve spring. The ultra high strength spring steel according to one embodiment of the present invention is a valve spring steel used for an engine of a vehicle 0.5 to 0.7% of Cr, 1.2 to 1.5% of Si, 0.6 to 1.2% of Mn, 0.6 to 1.2% of Cr, 0.1 to 0.5% of Mo, 0.05 to 0.8% (Excluding 0%), Al: 0.0001 to 0.3%, N: 0.03% or less (excluding 0%), O: 0.0001 To 0.003%, the balance Fe and other unavoidable impurities.
Description
The present invention relates to an ultra high strength spring steel, and more particularly, to an ultra high strength spring steel which is improved in tensile strength and fatigue life so as to be usable for an engine valve spring.
Due to the limit of fossil fuel reserves, continuous surge in international oil prices, and rapid changes, interest in improving fuel efficiency of vehicles has been greatly increased.
In order to improve fuel efficiency, it is important not only to reduce the weight loss of the vehicle body and the friction loss of each system link, but also to maximize the output efficiency by improving the dynamic characteristics in the combustion control of the engine itself. Efforts are being made to improve fuel economy by reducing dynamic loads.
Among the dynamic behavior parts, the engine valve spring directly controls the dynamic load and is a fuel-efficient part when it is lightweight. Conventional valve springs are mainly made of CrSi steel having a tensile strength of 1900 MPa and CrSiV having a strength of 2100 MPa. Further, efforts have been made to develop a high strength spring steel having a tensile strength of 2100 MPa or more by adding an alloy element to the existing CrSiV steel .
The present invention provides an ultra-high strength spring steel having an excellent fatigue strength by controlling inclusions that have better tensile strength and improved fatigue life than conventional ones by optimizing Mo, Ni, V, Nb and Ti contents.
The ultra-high strength spring steel according to one embodiment of the present invention is a valve spring steel used in an engine of a vehicle. The spring steel comprises 0.5 to 0.7% of C, 1.2 to 1.5% of Si, 0.6 to 1.2% of Mn, : 0.05 to 0.5%, Nb: 0.05 to 0.5%, Ti: 0.05 to 0.3%, Cu: 0.3% or less (excluding 0%) ), Al: 0.0001 to 0.3%, N: 0.03% or less (excluding 0%), O: 0.0001 to 0.003%, balance Fe and other unavoidable impurities.
The spring steel has a yield strength of 2300 MPa or more.
The spring steel has a fatigue strength of 1100 MPa or more.
The spring steel has a tensile strength of 2800 MPa or more.
The spring steel has a hardness of 710 HV or more.
And the size of the inclusions present in the spring steel is 15 mu m or less.
The proportion of inclusions having a size of 10 to 15 占 퐉 in the inclusions is 10% or less, and the proportion of inclusions having a size of less than 10 占 퐉 is 90% or more.
According to the embodiment of the present invention, by optimizing the content of the main alloy component, not only the high strength of tensile strength of 2800 MPa or more, but also the inclusion of minute inclusions can be achieved, and ultra high strength spring steel having excellent physical properties of fatigue strength of 1100 MPa or more can be obtained.
1 is a table showing the components of Examples and Comparative Examples,
2 is a table showing physical properties and performances of Examples and Comparative Examples,
FIG. 3 is a graph showing a result of calculation of phase-dependent phase transformation of ultra-high strength spring steel according to an embodiment of the present invention,
FIG. 4 is a graph showing a result of calculation of a phase transformation according to temperature in a cementite structure of an ultra-high strength spring steel according to an embodiment of the present invention.
Hereinafter, embodiments of the present invention will be described in detail with reference to the accompanying drawings. It will be apparent to those skilled in the art that the present invention may be embodied in many different forms and should not be construed as limited to the embodiments set forth herein. Rather, these embodiments are provided so that this disclosure will be thorough and complete, It is provided to let you know.
FIG. 1 is a graph showing a result of calculation of phase-dependent phase transformation of an ultra-high strength spring steel according to an embodiment of the present invention. FIG. 2 is a graph showing a result of calculation of a phase transformation according to temperature in a cementite structure of an ultra- It is a graph showing.
The ultra-high strength spring steel according to the present invention is a spring steel which is used as a valve spring steel for an engine of a vehicle and which improves physical properties such as tensile strength and fatigue strength by optimizing the content of major alloy components. Concretely, in terms of% by weight, at least one member selected from the group consisting of 0.5 to 0.7% of C, 1.2 to 1.5% of Si, 0.6 to 1.2% of Mn, 0.6 to 1.2% of Cr, 0.1 to 0.5% of Mo, (Excluding 0%), Al: 0.0001-0.3%, N: 0.03% or less, V: 0.05-0.5%, Nb: 0.05-0.5% O: 0.0001 to 0.003%, the balance Fe and other unavoidable impurities.
In the present invention, the reason for limiting the alloy components and the composition ranges thereof is as follows. Hereinafter, unless otherwise specified, the percentages expressed in terms of the composition range means% by weight.
The carbon (C) preferably contains 0.5 to 0.7%. The carbon content in the steel is proportional to the increase in strength. When the carbon content is less than 0.5%, the increase in strength is insignificant due to insufficient penetration at the heat treatment. When the carbon content exceeds 0.7%, martensite structure is formed at the time of incineration, fatigue strength is decreased, do. Within this range, it is possible to secure high strength and ductility.
The silicon (Si) preferably contains 1.2 to 1.5%. Silicon is an element that improves elongation, improves heat resistance and hardenability, and suppresses change of shape to improve permanent set property (shape retention). Further, the ferrite and martensite structure are cured and solidified in the ferrite to increase the strength and the softening softening resistance. When the content is less than 1.2%, the resistance to softening is low. When the content is more than 1.5%, the heat resistance is improved, but it is sensitive to decarburization, thereby causing decarburization during heat treatment.
It is preferable that manganese (Mn) contains 0.6 to 1.2%. Manganese is an element which improves hardenability and strength and is dissolved in a matrix to increase the bending fatigue strength and incombustibility and inhibit the formation of inclusions such as Al 2 O 3 as a deoxidizer for producing oxides. When the content is less than 0.6%, it is difficult to secure the entrapment property, and when the content exceeds 1.2%, the toughness deteriorates.
Cr (Cr) preferably contains 0.6 to 1.2%. Chromium is used for toughness to form precipitates during tempering. It improves hardenability, suppresses softening, improves strength, and contributes to grain refinement and toughness. In terms of softening, decarburization, incombustibility and corrosion resistance, the effect is excellent at 0.6% or more. When the content exceeds 1.2%, the grain boundary carbide is excessively generated, and the strength and brittleness problems are caused.
The molybdenum (Mo) content is preferably 0.1 to 0.5%. Molybdenum forms fine precipitated carbides like Cr to improve strength and fracture toughness. Particularly, TiMoC of 1 to 5 nm is uniformly formed to improve the tempering resistance, and heat resistance and high strength are ensured. When it is less than 0.1%, carbide generation is impossible and sufficient strength can not be ensured. The synergistic effect is saturated and it is not necessary to contain more than the cost.
Nickel (Ni) preferably contains 0.05 to 0.8%. Nickel is an element that helps improve corrosion resistance. It improves heat resistance, prevents low temperature brittleness, improves hardenability, improves dimensional invariance and settability. When the content is less than 0.05%, the corrosion resistance and high temperature stability are deteriorated, and when the content is more than 0.8%, there arises a problem that heat and brittleness are generated.
It is preferable to contain 0.05 to 0.5% of vanadium (V). Vanadium improves the fracture toughness by forming VC which is a micro precipitate as an element which improves texture refinement, resistance to tempering, dimensional invariance and settability, and ensures heat resistance and high strength. In particular, VC, which is a fine precipitate, inhibits crystal grain boundary migration, the austenizing V is dissolved and dissolved, and precipitates at the time of tempering to cause secondary curing. If the content is less than 0.05%, the effect of preventing the fracture toughness from lowering is reduced, and when the content exceeds 0.5%, the size of the precipitate becomes large and the post-hardness becomes low.
It is preferable that niobium (Nb) contains 0.05 to 0.5%. Niobium fine-grains the tissue, hardens the surface through nitriding, and improves dimensional invariance and settling. NbC is formed to improve the strength and control the generation rate of other carbides (CrC, VC, TiC, MoC). When the content is less than 0.05%, there arises a problem of reduction in strength and non-uniformity of carbide, and when 0.5% or more, generation of other carbides is inhibited.
Titanium (Ti) is preferably contained in an amount of 0.05 to 0.3%. Titanium, like Nb, Al, etc., prevents grain recrystallization and inhibits growth. Also, titanium forms nanocarbides such as TiC and TiMoC, reacts with nitrogen, inhibits grain growth by generating TiN, and forms TiB 2 , thereby preventing B from bonding with N, thereby minimizing the degradation of BN do. If the content is less than 0.05%, other inclusions such as Al 2 O 3 are generated and the fatigue endurance is lowered. If the content is more than 0.3%, the effect of other alloying elements is hindered and the cost increases.
Copper (Cu) preferably contains 0.3% or less (excluding 0%). Copper is an element that improves quenching and strength after tempering and improves the corrosion resistance of steel like Ni. However, since the cost of the alloy is increased in the case of excessive content, it is preferable to limit the content to 0.3% or less.
Aluminum (Al) is preferably contained in an amount of 0.0001 to 0.3%. Aluminum reacts with nitrogen and forms AlN, thereby making the austenite finer and improving the strength and impact toughness. In particular, it can be added together with Nb, Ti, and Mo to reduce the addition amount of vanadium for grain refinement and nickel for toughness, which are expensive elements. When the content is less than 0.0001%, effects due to the inclusion can not be expected. When the content is more than 0.3%, a square-type large inclusion (Al 2 O 3 ) is generated and these angular inclusions act as fatigue starting points to weaken the steel, .
It is preferable that nitrogen (N) contains 0.03% or less (excluding 0%). Nitrogen reacts with Al and Ti to form AlN and TiN, thereby exerting a grain refining effect and maximizing boron inclusion by TiN formation. However, the excess content causes deterioration of the ingot strength due to the reaction with boron, so that the content thereof is preferably limited to 0.03% or less.
The oxygen (O) content is preferably 0.0001 to 0.003%. Oxygen bonds with Si or Al to form hard oxide-based nonmetallic inclusions, which causes deterioration in fatigue life characteristics. Therefore, it is desirable to keep the content as low as possible. However, keeping oxygen at less than 0.0001% In the present invention, up to 0.003% is allowed.
On the other hand, the remainder other than the above-mentioned components are Fe and inevitably contained impurities.
Hereinafter, the present invention will be described using comparative examples and examples.
Experiments were conducted to produce spring steel according to Examples and Comparative Examples according to the production conditions of commercially produced spring steels. As shown in FIG. 1, the wire rod produced through the produced molten steel while changing the content of each component was heat- , Quench-bellows and lead-bell-clinking are sequentially fabricated into a steel wire. Specifically, the wire rod is maintained at 940 to 960 ° C. for 3 to 5 minutes, then rapidly cooled to 640 to 660 ° C., maintained at this temperature for 2 to 4 minutes, and then cooled to 18 to 22 ° C. for 0.5 to 1.5 minutes. Such a constant-temperature heat treatment is carried out so as to facilitate the drawing as a post-process, and pearlite is produced in the wire rod through the heat treatment.
The thermo-thermally treated wire rod is made into a target wire rod through several stages of drawing process. In the present invention, it was fresh with 3.3 mm wire.
The dried wire rod is heated again and maintained at 940 to 960 ° C for 3 to 5 minutes, quenched to 45 to 55 ° C and squeezed for 0.5 to 1.5 minutes. Thereafter, the wire rod is heated to 440 to 460 ° C, held for 2 to 4 minutes, Through the ingestion, martensite is formed on the wire to ensure strength, and tempered martensite is formed on the surface through the lead-free solder to ensure strength and toughness.
Next, test examples for confirming the physical properties of the spring steel according to the above-described Examples and Comparative Examples will be described.
The tensile strength, yield strength, hardness, fatigue strength, formability, fatigue life and inclusion regulation of the spring steel according to each of the examples and comparative examples were tested, and the results are shown in Fig.
The yield strength and the tensile strength were measured with a 20-ton tester according to KS B 0802, and the hardness was measured at 300 gf using a micro-Vickers hardness meter according to KS B 0811. The fatigue strength And fatigue life were measured by rotary bending fatigue test according to KS B ISO 1143, and moldability was evaluated as follows. The mold springs were manufactured with valve diameter of 6.5 / Respectively.
Inclusions regulation Max with respect to the next along the center line was cut and collected, the area 60 mm 2 parallel to the rolling of each sample. The maximum size of the B-system and C-system inclusions existing on the surface to be inspected was measured using the t-method. At this time, the microscope magnification was measured at 400 to 500 times. When no inclusions having a fraction of the inclusions exceeding 15 탆 were found, the inclusions having 10 to 15 탆 were less than 10% and the inclusions having 10 탆 were not less than 90% Respectively. In this case, the B-system inclusions are aggregated in the processing direction discontinuously and the granular inclusions are aggregated. For example, they may be alumina-based (Al 2 O 3 ) inclusions. C-system inclusions are not viscously deformed and are irregularly dispersed For example, silicate-based (SiO 2 ) inclusions.
As can be seen from FIG. 2, the conventional steel passed through regulations on formability and inclusion due to the non-content of Mo, Ni, V, Nb and Ti, but the present invention Of the present invention.
Comparative Examples 1 to 12 are examples in which the content of the alloy component specified in the present invention is not satisfied and the tensile strength, the yield strength, the hardness, the fatigue strength, the moldability and the fatigue life of the conventional steel are partially improved But did not meet all the requirements of the present invention.
In particular, in Comparative Example 1, since the Mo content was low and the yield strength was not sufficiently secured, the improvement of the tensile strength and the yield strength of the conventional steel was insufficient, and the hardness, fatigue strength, formability and fatigue life were rather reduced.
In Comparative Example 2, Comparative Example 3, Comparative Example 6, Comparative Example 9, and Comparative Example 10 did not satisfy the regulatory requirements for Mo, Ni, V, and Ti contents, respectively. It was confirmed that the inclusions did not pass the regulation of the inclusions due to the coarsening of the inclusions, the unevenness of the molten steel during the steelmaking process, and the influences on the formation of inclusions.
In Comparative Example 9, when the content of Ti is less than the specified requirement, generation of other inclusions such as Al 2 O 3 is promoted and the fatigue endurance is lowered. Therefore, the fatigue strength and fatigue life are comparable to those of the conventional steel, .
On the other hand, Examples 1 to 3 all exhibited a yield strength of 2300 MPa or higher and a tensile strength of 2800 MPa or higher as the inventive steel satisfying all the requirements of the present invention, and the hardness was 710 HV or higher. In addition, the fatigue strength was more than 1100 MPa, and passed all the moldability and inclusion regulation. And the fatigue life was over 400,000 times.
FIG. 3 is a graph showing the results of calculation of phase-dependent phase transformation of ultra-high strength spring steel according to an embodiment of the present invention. FIG. 4 is a graph showing the phase transformation of super- This is a graph showing the results.
FIG. 3 is a graph showing the temperature-dependent phase transformation calculation results for an embodiment having an alloy composition such as Fe-1.4Si-0.7Mn-0.7Cr-0.55C-0.3Ni-0.1Mo-0.1V, It can be expected that strength enhancement and fatigue life improvement can be expected by generating FCC-A1 (austenite), BCC-A2 (ferrite), Cementite and various carbides (CrC, VC, etc.).
Fig. 4 also shows a graph showing the results of calculation of the phase transformation in the cementite structure of spring steel according to the embodiment having an alloy composition such as Fe-1.4Si-0.7Mn-0.7Cr-0.55C-0.3Ni-0.1Mo-0.1V , It can be predicted that the complex behavior of 7- to 8-member elements in the cementite can be predicted, and thus it is expected that the fine carbide can be uniformly distributed.
Although the present invention has been described with reference to the accompanying drawings and the preferred embodiments described above, the present invention is not limited thereto but is limited by the following claims. Accordingly, those skilled in the art will appreciate that various modifications and changes may be made thereto without departing from the spirit of the following claims.
Claims (7)
The steel sheet according to any one of claims 1 to 3, wherein the steel sheet contains 0.5 to 0.7% of C, 1.2 to 1.5% of Si, 0.6 to 1.2% of Mn, 0.6 to 1.2% of Cr, 0.1 to 0.5% of Mo, 0.05 to 0.8% of Ni, (Excluding 0%), Al: 0.0001 to 0.3%, N: 0.03% or less (excluding 0%), O: 0.0001 to 0.5%, Nb: 0.05 to 0.5% 0.003%, the balance Fe and other unavoidable impurities, and has a tensile strength of 2800 MPa or more and a hardness of 710 HV or more.
Wherein the spring steel has a yield strength of 2300 MPa or more.
Wherein the spring steel has a fatigue strength of 1100 MPa or more.
Wherein said spring steel has a fatigue life of at least 400,000 times as measured by rotational bending fatigue testing of the test specimen according to KS B ISO 1143.
And the size of the inclusions present in the spring steel is 15 占 퐉 or less.
Wherein a fraction of the inclusions having a size of 10 to 15 占 퐉 is 10% or less, and a fraction occupied by inclusions having a size of less than 10 占 퐉 is 90% or more.
Priority Applications (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR1020150171889A KR101745191B1 (en) | 2015-12-04 | 2015-12-04 | Ultra high strength spring steel |
| US15/091,448 US20170159158A1 (en) | 2015-12-04 | 2016-04-05 | Ultra-high-strength spring steel |
| DE102016107787.9A DE102016107787A1 (en) | 2015-12-04 | 2016-04-27 | Ultrahigh-strength spring steel |
| CN201610285110.6A CN106834954A (en) | 2015-12-04 | 2016-04-29 | Superhigh intensity spring steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR1020150171889A KR101745191B1 (en) | 2015-12-04 | 2015-12-04 | Ultra high strength spring steel |
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| KR101745191B1 true KR101745191B1 (en) | 2017-06-09 |
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| Application Number | Title | Priority Date | Filing Date |
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| KR1020150171889A KR101745191B1 (en) | 2015-12-04 | 2015-12-04 | Ultra high strength spring steel |
Country Status (4)
| Country | Link |
|---|---|
| US (1) | US20170159158A1 (en) |
| KR (1) | KR101745191B1 (en) |
| CN (1) | CN106834954A (en) |
| DE (1) | DE102016107787A1 (en) |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN107587068A (en) * | 2017-10-16 | 2018-01-16 | 武汉钢铁有限公司 | A kind of tensile strength >=2100MPa spring steel and production method |
| CN107723596A (en) * | 2017-10-16 | 2018-02-23 | 武汉钢铁有限公司 | A kind of excellent spring steel of anti-fatigue performance and elasticity attenuation resistance energy and production method |
| CN110760748B (en) * | 2018-07-27 | 2021-05-14 | 宝山钢铁股份有限公司 | Spring steel with excellent fatigue life and manufacturing method thereof |
| CN111334707B (en) * | 2018-12-18 | 2021-12-14 | 南京工程学院 | Variable cross-section spring leaf with uniform structure and grain refinement and manufacturing method thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100213542B1 (en) * | 1995-10-27 | 1999-08-02 | 구마모토 마사히로 | Spring steel with excellent resistance to hydrogen embrittlement and fatigue |
| JP2012072492A (en) | 2010-08-30 | 2012-04-12 | Kobe Steel Ltd | Steel wire material for high-strength spring having excellent wire-drawing property and method for producing the same, and high-strength spring |
-
2015
- 2015-12-04 KR KR1020150171889A patent/KR101745191B1/en active IP Right Grant
-
2016
- 2016-04-05 US US15/091,448 patent/US20170159158A1/en not_active Abandoned
- 2016-04-27 DE DE102016107787.9A patent/DE102016107787A1/en not_active Withdrawn
- 2016-04-29 CN CN201610285110.6A patent/CN106834954A/en active Pending
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100213542B1 (en) * | 1995-10-27 | 1999-08-02 | 구마모토 마사히로 | Spring steel with excellent resistance to hydrogen embrittlement and fatigue |
| JP2012072492A (en) | 2010-08-30 | 2012-04-12 | Kobe Steel Ltd | Steel wire material for high-strength spring having excellent wire-drawing property and method for producing the same, and high-strength spring |
Also Published As
| Publication number | Publication date |
|---|---|
| CN106834954A (en) | 2017-06-13 |
| DE102016107787A1 (en) | 2017-06-08 |
| US20170159158A1 (en) | 2017-06-08 |
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