WO2004035848A1 - 転造性、耐焼割れ性およびねじり特性に優れた機械構造用鋼材およびドライブシャフト - Google Patents
転造性、耐焼割れ性およびねじり特性に優れた機械構造用鋼材およびドライブシャフト Download PDFInfo
- Publication number
- WO2004035848A1 WO2004035848A1 PCT/JP2002/013564 JP0213564W WO2004035848A1 WO 2004035848 A1 WO2004035848 A1 WO 2004035848A1 JP 0213564 W JP0213564 W JP 0213564W WO 2004035848 A1 WO2004035848 A1 WO 2004035848A1
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- WIPO (PCT)
- Prior art keywords
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- steel material
- drive shaft
- steel
- rolling
- Prior art date
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Classifications
-
- 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
-
- 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
-
- 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
-
- 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
Definitions
- Machine structural steel and drive shafts with excellent rollability, fire resistance and torsion properties are Machine structural steel and drive shafts with excellent rollability, fire resistance and torsion properties
- the present invention relates to a steel material for a machine structure.
- the present invention relates to a steel for machine structural use having excellent rollability, resistance to fire cracking and torsion characteristics.
- the present invention provides a steel material for machine structural use manufactured using electric furnace material instead of blast furnace material, which does not deteriorate in the above-mentioned characteristics even when mixed with tramp elements such as Cu and Ni. Background art
- the required torsional strength is required for components for mechanical structures such as automobile drive shafts and constant velocity joints.
- hot-rolled steel bars are generally hot forged, if necessary, subjected to normalizing treatment, processed into a predetermined shape by cutting, cold forging, etc. Quenched and tempered.
- the body weight has been reduced for the purpose of improving fuel efficiency of automobiles. It is desired to improve the torsional strength of automotive parts in order to reduce the weight of automotive parts.
- machinability and resistance to fire cracking of steel are required.
- induction hardening may increase the quenching hardness and quenching depth.
- the only way to increase the quench hardness and depth is to change the induction hardening conditions or increase the amount of alloying elements in the steel, both of which increase manufacturing costs.
- a technique has been proposed in which the amount of alloying elements is limited, as shown in Patent Document 1, for example.
- the inventors first adjusted the composition of the steel material and simultaneously controlled the steel structure, so that, for example, as shown in Patent Document 2, We proposed a steel material for machine structures that has excellent cracking and torsion characteristics.
- Patent Document 1 JP-A-4-218641 (Claims)
- Patent Document 2 Japanese Patent No. 3288563 (Claims)
- An object of the present invention is to solve the above problems. In other words, even if an electric furnace material is used instead of a blast furnace material, the rollability is effectively prevented from being deteriorated, and a steel material for machine structural use having both excellent resistance to fire cracking and torsion characteristics is provided. Purpose. Further, the invention proposes a drive shaft formed using this steel material.
- the inventors have conducted intensive studies to achieve the above object and have obtained the following findings.
- Mn 0.2% or more, 1.1% or less
- Al 0.01% or more, 0.05% or less
- Ni 0.05% or more, 0.2% or less
- C, Mn, P, S, Si, Cr, Ni, Mo, and Cu in the formula mean the content (% by mass) of each element. 2.
- the steel material is further
- V 0.01% or more, 0.30% or less
- Nb 0.005% or more, 0.050% or less
- a steel material for machine structural use having excellent rollability, quenching crack resistance and torsion characteristics characterized by having a composition containing
- Figure 1 shows the effect of the LD value on rollability.
- Fig. 2 shows the results of measuring the static strength of the drive shaft by the static strength test.
- FIG. 3 shows the results of measuring the fatigue strength of the drive shaft of the invention example and the drive shaft of the comparative example by a fatigue strength test.
- C is the element that has the greatest effect on induction hardening, and is useful in increasing the hardness and depth of the quenched hardened layer and ensuring torsional strength of 1400 MPa or more after induction hardening and tempering.
- the content is less than 0.35%, the effect of the addition is poor, while if it exceeds 0.50%, the machinability and the resistance to cracking are reduced, so the C content is 0.35% or more.
- the range was limited to 0.50% or less.
- Si 0.15% or less
- Si is an element that enhances torsional strength by strengthening steel by forming a solid solution in ferrite in addition to acting as a deoxidizing element, and is preferably added in an amount exceeding 0.05%.
- the Si content exceeds 0.15%, the machinability is significantly deteriorated, so the range is limited to 0.15% or less.
- Mn 0.2% or more, 1.1% or less
- ⁇ is a useful element that contributes to the improvement of torsional strength by improving hardenability and increasing the hardness depth during induction hardening.
- the content is less than 0.2%, the effect of the addition is poor.On the other hand, if it exceeds 1.1%, not only rollability but also machinability and torsional strength are deteriorated, so the Mn content is 0.2% or more and 1.1%. Limited to the following range. Preferably, it is in the range of 0.2% or more and 0.8% or less.
- P segregates at the austenite grain boundary during quenching and promotes the occurrence of quenching cracks. Therefore, it is preferable to reduce P as much as possible. From this viewpoint, P is set to 0.020% or less.
- the content of S was set to 0.005% or more.
- the upper limit of the amount of S was limited to 0.035%. Preferably, it is in the range of 0.010% or more and 0.035% or less.
- Cr is a particularly important element in the present invention, and the inclusion of Cr advantageously eliminates the adverse effects of Trump elements, such as Cu and Ni, which cause deterioration in rollability, torsion properties, machinability, etc. be able to.
- Trump elements such as Cu and Ni
- the Cr content is less than 0.1%, the effect of the addition is poor, while if it exceeds 0.2%, the rollability, machinability and torsional strength decrease, so Cr is contained in the range of more than 0.1% and 0.2% or less. I was to make it.
- Mo 0.05% or more, 0.5% or less Mo is useful not only for improving hardenability but also for promoting the formation of bainite and improving machinability.
- the content of 0.05% or more is required, but if it exceeds 0.5%, the machinability is rather deteriorated. Therefore, the Mo content is limited to the range of 0.05% or more and 0.5% or less. Preferably, it is in the range of 0.1% or more and 0.5% or less.
- Ti combines with N to form nitrides, and refines austenite grains during high-temperature heating. This element is necessary to secure solid solution B useful for improving hardenability. For that purpose, the content of 0.01% or more is required, but if it exceeds 0.05%, the toughness is impaired, so the Ti content is limited to the range of 0.01% or more and 0.05% or less.
- A1 0.01% or more, 0.05% or less
- A1 is useful as a deoxidizer, and at least 0.01% must be contained for this purpose.However, if it exceeds 0.05%, giant alumina is generated, which becomes the starting point of fatigue fracture and causes fatigue strength. Therefore, the amount of A1 was limited to the range of 0.01% or more and 0.05% or less.
- N is a useful element that combines with A1 and Ti to form nitrides and improves the fatigue strength by reducing the austenite grain size during high-frequency heating.
- the content exceeds 0.01%, the nitride coarsens and conversely deteriorates the fatigue strength.
- Excessive addition of N also has the disadvantage of forming BN and lowering the amount of solid solution B effective for hardenability. Therefore, the N content was limited to 0.01% or less.
- B has the effect of improving the hardenability and increasing the quenching depth during induction hardening, thereby improving the torsional strength. For this purpose, 0.0005% or more must be added, but if it exceeds 0.0050%, the toughness is deteriorated. Therefore, B is limited to the range of 0.0005% or more and 0.0050% or less.
- Cu 0.06% or more, 0.25% or less Cu is an element that is inevitably mixed as a playing element. If the content exceeds 0.25%, the rollability and the like will deteriorate, so the content is set to 0.25% or less. On the other hand, if it is reduced to less than 0.06%, the production cost is increased.
- Ni 0.05% or more, 0.2% or less
- Ni is an element that is inevitably mixed as a tramp element. If the content exceeds 0.2%, the rollability and the like will deteriorate, so the content is set to 0.2% or less. On the other hand, if the content is reduced to less than 0.05%, the production cost is increased.
- V 0.01% or more, 0.30% or less
- Nb 0.005% or more, 0.050% or less
- V and Nb form carbonitrides and refine the austenite grains, effectively contributing to the improvement of strength.
- V and Nb contents are less than 0.01%, respectively.
- Nb Limited to the range of 0.005% or more and 0.050% or less.
- C, Mn, P, S, Si, Cr, Ni, Mo, and Cu in the formula mean the content (% by mass) of each element.
- This LD value is an index of hardness and structure through hardenability.
- FIG. 1 shows the results of examining the effect of the above-mentioned LD value on the rollability of the high Cr and high Si steels according to the present invention. Also, in the figure, for comparison, The results of investigations on low Cr and low Si steels described in Patent Document 2 are also shown.
- the die life sharply decreases.However, the die life in the range where the LD value is 120 or less, that is, the rolling property, is higher than that of the present invention. High Si steels are much better.
- component adjustment is performed so that the above-mentioned LD value becomes 120 or less.
- the steel structure is not particularly limited, but is preferably a structure mainly composed of ferrite and containing a bainite phase in an area ratio of about 5 to 30%.
- the steel material of the present invention described above is most suitable for use in power transmission parts, particularly in driveshafts for automobiles and constant velocity joints. Not only is the workability excellent, but also the load capacity is increased, so that there is a great effect that the weight can be reduced.
- the method for producing the steel material of the present invention is not particularly limited as long as it is produced according to a conventional method.
- the steel for machine structural use provided by the present invention has good rollability even if it contains Cu or Ni, which is difficult to remove by melting using an electric furnace. Particularly suitable for manufacturing. Vacuum degassing such as RH degassing, refining with a ladle, etc. may be added.
- the molten steel is solidified by a continuous casting method or an ingot casting method, solidified, and then subjected to hot rolling or hot / warm forging to obtain a material having a predetermined shape. These materials are subjected to an intermediate heat treatment such as normalizing, spheroidizing annealing, softening annealing and the like, if necessary, and finished to a desired shape by cold working such as cutting, forging, and rolling.
- hot rolling, hot forging, or normalizing is performed to finish the product shape.
- the cooling after austenitization such as after hot rolling or hot forging and further normalizing is preferably about 0.2 to 2.0 / s in order to produce an appropriate amount of bainite. .
- Fast cooling is preferred.
- the final induction quenching and tempering was performed using an induction quenching device of about 15 kHz, heating at about 120 kW for about 0.2 to 1.0 seconds, then quenching, and heating at 170 ° C for 30 minutes. What is necessary is just to give a degree of tempering.
- Table 2 shows the results obtained by examining the microstructure, rollability, torsion characteristics, and quenching crack resistance of the steel bars thus obtained.
- the method of evaluating the structure of the steel and each characteristic is as follows.
- the microstructure of the cooled straight bar was photographed with an optical microscope, the steel structure was identified from this photograph, and the area ratio of the bainite phase was measured with an image analyzer.
- Rollability was evaluated by the die life in the rolling test.
- the die life was evaluated by the number of materials that could be rolled before rolling became impossible due to chipping of the dies, peeling of the fracture surface, and abrasion of the teeth.
- the die material is SKD11, and the spline specifications are as follows.
- a parallel round torsion test piece with a parallel part: 20 o ⁇ was prepared from a straight bar, and quenched using a 15 kHz frequency induction hardening device and tempered at 170 ° C for 30 min. After that, a torsion test was performed. The quenching depth after induction hardening and tempering was about 4 ram. In the torsion test, the maximum torsional shear strength was determined using a 4900 J (500 kgf ⁇ m) torsion tester, and this was defined as the torsional strength.
- the resistance to quenching cracking was determined by processing a straight bar of 25 ⁇ above into a round bar (20 band ⁇ ) with an axial V-shaped groove on the surface, and performing the same induction hardening as in (3) above. Then, 10 places in the C section of the round bar were polished and observed, and the number of cracks generated was evaluated.
- the machinability test was performed using a SKH 4, 4 ⁇ ⁇ ⁇ ⁇ drill, drilling 12 band lengths under the condition of rotation speed: 1500 rpm, and the total drilling length until cutting became impossible ( ⁇ ) was evaluated, and this was evaluated as the tool life.
- all of the steel materials obtained according to the present invention have excellent rollability, torsion characteristics, fire cracking resistance and machinability.
- the static strength and fatigue strength of a drive shaft formed using a steel material according to the present invention and provided with a hardened layer by induction hardening and tempering will be described with reference to FIGS. 2 and 3, respectively.
- the drive shaft of the invention example was manufactured using the steel material of No. 2 in Table 1.
- the drive shaft of the comparative example was manufactured using the steel material of No.
- Figure 2 shows the results of measuring the static strength of the drive shaft by the static strength test.
- the static strength test measures the maximum torque at the time of drive shaft failure and evaluates the static strength.
- the number of drive shafts subjected to the test is one in the comparative example and two in the invention example. In FIG. 2, they are represented as Comparative Example, Invention Example 1, and Invention Example 2, respectively.
- the maximum torque that acts when the drive shaft of the comparative example breaks is set to 1
- the maximum torque that acts when the drive shaft of the invention breaks is represented by a ratio to the maximum torque.
- the drive shaft of the invention example has about 1.17 times higher static strength than the drive shaft of the comparative example. I understand.
- FIG. 3 shows the results of measuring the fatigue strength of the drive shaft of the invention example and the drive shaft of the comparative example by a fatigue strength test.
- the fatigue strength test is a test to measure the fatigue strength when repeatedly applying torque. A predetermined load torque is repeatedly applied to the drive shaft, and the number N of load repetitions until breakage is determined.
- the vertical axis is a value obtained by dividing the load torque by the static strength of the drive shaft of the comparative example, and is a dimensionless number.
- the horizontal axis is the number of repetitions of the load until the drive shaft breaks.
- the bad effect of a trump element can be removed from the steel material for machine structures manufactured using the electric furnace in which the tramp elements, such as Cu and Ni, are inevitably mixed. It is possible to obtain a steel material having excellent rolling properties, torsional properties, quenching crack resistance, and hardenability.
- the steel material according to the present invention is used for a power transmission component, in particular, a drive shaft or a constant velocity joint for an automobile, it has a great effect that not only excellent workability but also high strength and light weight can be achieved.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Articles (AREA)
- Heat Treatment Of Steel (AREA)
- Shafts, Cranks, Connecting Bars, And Related Bearings (AREA)
Description
Claims
Priority Applications (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE60222595T DE60222595T2 (de) | 2002-10-18 | 2002-12-26 | Stahlmaterial für mechanische konstruktionen mit hervorragender walzbarkeit, abschreckungsrissfestigkeit und torsionseigenschaft und antriebswelle |
US10/526,802 US20060065328A1 (en) | 2002-10-18 | 2002-12-26 | Steel material for mechanical structure excellent in suitability for rolling, quenching crack resistance, and torsional property and drive shaft |
EP02790877A EP1553197B1 (en) | 2002-10-18 | 2002-12-26 | Steel material for mechanical structure excellent in suitability for rolling, quenching crack resistance, and torsional property and drive shaft |
JP2004544722A JP4170294B2 (ja) | 2002-10-18 | 2002-12-26 | 転造性、耐焼割れ性およびねじり特性に優れた機械構造用鋼材およびドライブシャフト |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2002-304190 | 2002-10-18 | ||
JP2002304190 | 2002-10-18 |
Publications (1)
Publication Number | Publication Date |
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WO2004035848A1 true WO2004035848A1 (ja) | 2004-04-29 |
Family
ID=32105100
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
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PCT/JP2002/013564 WO2004035848A1 (ja) | 2002-10-18 | 2002-12-26 | 転造性、耐焼割れ性およびねじり特性に優れた機械構造用鋼材およびドライブシャフト |
Country Status (7)
Country | Link |
---|---|
US (1) | US20060065328A1 (ja) |
EP (1) | EP1553197B1 (ja) |
JP (1) | JP4170294B2 (ja) |
CN (1) | CN1307319C (ja) |
DE (1) | DE60222595T2 (ja) |
ES (1) | ES2292836T3 (ja) |
WO (1) | WO2004035848A1 (ja) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2023248556A1 (ja) * | 2022-06-24 | 2023-12-28 | Jfeスチール株式会社 | 高周波焼入れ用鋼 |
Families Citing this family (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
SE527221C2 (sv) * | 2005-04-12 | 2006-01-24 | Scania Cv Abp | Borstålsort för induktionshärdning jämte axel |
JP2007154305A (ja) * | 2005-07-05 | 2007-06-21 | Jfe Steel Kk | 強度、延性及び靱性に優れた機械構造用鋼およびその製造方法 |
KR102303599B1 (ko) * | 2017-05-18 | 2021-09-23 | 닛폰세이테츠 가부시키가이샤 | 선재, 강선, 및 강선의 제조 방법 |
JP7136320B2 (ja) * | 2019-03-05 | 2022-09-13 | 日本製鉄株式会社 | クランクシャフト |
Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
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JPH093592A (ja) * | 1995-06-19 | 1997-01-07 | Toa Steel Co Ltd | 冷間加工性および高周波焼入れ性に優れた機械構造用鋼 |
JPH0920958A (ja) * | 1995-06-30 | 1997-01-21 | Nkk Corp | 耐二次加工性に優れたプレス成形用熱延鋼板及びその製造方法 |
Family Cites Families (8)
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JPS61174322A (ja) * | 1985-01-28 | 1986-08-06 | Nippon Steel Corp | 機械構造用鋼の圧延材軟質化法 |
US5279688A (en) * | 1989-12-06 | 1994-01-18 | Daido Tokushuko Kabushiki Kaisha | Steel shaft material which is capable of being directly cut and induction hardened and a method for manufacturing the same |
JP3062275B2 (ja) * | 1990-05-02 | 2000-07-10 | 川崎製鉄株式会社 | 高強度軸部品用鋼材 |
JP3288563B2 (ja) * | 1995-10-17 | 2002-06-04 | 川崎製鉄株式会社 | 被削性および耐焼割れ性に優れた機械構造用鋼材およびその製造方法 |
CN1163942A (zh) * | 1996-02-08 | 1997-11-05 | 阿斯克迈塔尔公司 | 制造锻件用钢及锻件制造方法 |
JP3402562B2 (ja) * | 1996-07-19 | 2003-05-06 | 大同特殊鋼株式会社 | 高周波焼入れ部品 |
DE69811200T2 (de) * | 1997-07-22 | 2003-10-09 | Nippon Steel Corp | Einsatzstahl mit hervorragender verhinderung der sekundärrekristallisation während der aufkohlung, verfahren zu dessen herstellung, halbzeug für aufzukohlende teile |
JP2000154828A (ja) * | 1998-11-19 | 2000-06-06 | Nippon Steel Corp | 耐フレーキング特性と軸部強度に優れた等速ジョイント用外輪とその製造方法 |
-
2002
- 2002-12-26 JP JP2004544722A patent/JP4170294B2/ja not_active Expired - Lifetime
- 2002-12-26 DE DE60222595T patent/DE60222595T2/de not_active Expired - Lifetime
- 2002-12-26 ES ES02790877T patent/ES2292836T3/es not_active Expired - Lifetime
- 2002-12-26 WO PCT/JP2002/013564 patent/WO2004035848A1/ja active IP Right Grant
- 2002-12-26 CN CNB028297733A patent/CN1307319C/zh not_active Expired - Fee Related
- 2002-12-26 EP EP02790877A patent/EP1553197B1/en not_active Expired - Fee Related
- 2002-12-26 US US10/526,802 patent/US20060065328A1/en not_active Abandoned
Patent Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH093592A (ja) * | 1995-06-19 | 1997-01-07 | Toa Steel Co Ltd | 冷間加工性および高周波焼入れ性に優れた機械構造用鋼 |
JPH0920958A (ja) * | 1995-06-30 | 1997-01-21 | Nkk Corp | 耐二次加工性に優れたプレス成形用熱延鋼板及びその製造方法 |
Non-Patent Citations (1)
Title |
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See also references of EP1553197A4 * |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2023248556A1 (ja) * | 2022-06-24 | 2023-12-28 | Jfeスチール株式会社 | 高周波焼入れ用鋼 |
JP7485234B1 (ja) | 2022-06-24 | 2024-05-16 | Jfeスチール株式会社 | 高周波焼入れ用鋼 |
Also Published As
Publication number | Publication date |
---|---|
CN1688733A (zh) | 2005-10-26 |
US20060065328A1 (en) | 2006-03-30 |
DE60222595D1 (de) | 2007-10-31 |
JPWO2004035848A1 (ja) | 2006-02-16 |
EP1553197A4 (en) | 2006-07-05 |
DE60222595T2 (de) | 2008-06-19 |
EP1553197B1 (en) | 2007-09-19 |
ES2292836T3 (es) | 2008-03-16 |
JP4170294B2 (ja) | 2008-10-22 |
EP1553197A1 (en) | 2005-07-13 |
CN1307319C (zh) | 2007-03-28 |
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