CN1307319C - Steel material for mechanical structure excellent in suitability for rolling, quenching crack resistance, and torsional property and drive shaft - Google Patents
Steel material for mechanical structure excellent in suitability for rolling, quenching crack resistance, and torsional property and drive shaft Download PDFInfo
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- CN1307319C CN1307319C CNB028297733A CN02829773A CN1307319C CN 1307319 C CN1307319 C CN 1307319C CN B028297733 A CNB028297733 A CN B028297733A CN 02829773 A CN02829773 A CN 02829773A CN 1307319 C CN1307319 C CN 1307319C
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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
- C22C38/001—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
- C22C38/18—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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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Abstract
A machine structural steel product having superior formability of rotary-forming, torsional properties, and quenching-crack resistance is provided which is manufactured using an electric furnace instead of a blast furnace and which removes adverse influences of tramp elements. A drive shaft having a superior static strength and fatigue strength is provided. In particular, the machine structural steel product contains: on a mass percent basis, C: 0.35% to 0.50%; Si: 0.15% or less; Mn: 0.20% to 1.1%; P: 0.02% or less; S: 0.005% to 0.035%; Cr: more than 0.1% to 0.2%; Mo: 0.05% to 0.5%; Ti: 0.01% to 0.05%; Al: 0.01% to 0.05%; N: 0.01% or less; B: 0.0005% to 0.0050%; Cu: 0.06% to 0.25%; and Ni: 0.05% to 0.2%, and in addition, the composition described above is adjusted so that an LD value represented by the following equation (1) satisfies 120 or l.
Description
Technical field
The present invention relates to a kind of machine structural steel product.Be particularly related to the machine structural steel product of rollforming, quenching crack resistance and torsional property excellence.The machine structural steel product that uses the electric furnace material to replace the blast furnace material to make is provided, even these steel are sneaked into tramp elements such as Cu and Ni, above-mentioned all characteristics are deterioration not also.
Background technology
Require have required torsional strength with physical constructions such as transmission shaft and constant velocity cardan joints with member for automobile.In order to ensure torsional strength, the past is usually with the forge hot of hot rolling bar steel, and necessary occasion is implemented normalizing treatment, is processed into after the shape of defined enforcement high-frequency quenching, tempering by cutting, cold forging etc.
In order to protect environment, be the weight saving that purpose is being sought car body in recent years with the oil consumption that improves automobile.In order to alleviate the weight of trolley part, wish to improve the torsional strength of automobile with member.On the other hand, in the manufacturing process of trolley part, require machinability, the quenching crack resistance of steel.
In order to improve torsional strength, considering increases quenching hardness and depth of hardening by high-frequency quenching., increase only change high-frequency quenching condition or increase the alloying element amount of steel of the quenching hardness and the degree of depth, manufacturing cost all increases.In order to satisfy automobile simultaneously, for example shown in patent documentation 1, proposed to define the technology of alloying element amount with the torsional strength of member and machinability, quenching crack resistance.
, only adopt above-mentioned technology limiting chemical ingredients, the compositing range that can satisfy machinability, quenching crack resistance and torsional property simultaneously is very narrow, has this problem.In addition, also has the instability quality problem.
So as solution of the above problems, the inventor is by when the one-tenth of adjusting steel is grouped into, the control structure of steel for example shown in patent documentation 2, has taken the lead in proposing the machine structural steel product of machinability, quenching crack resistance and torsional property excellence.
Patent documentation 1: the spy opens flat 4-218641 communique (claims)
Patent documentation 2: No. 3288563 communique of patent (claims)
, when using electric furnace to make above-mentioned patent documentation 2 disclosed machine structural steel products, can not get desired characteristic, distinguish that especially the rollforming reduction is remarkable.With the blast furnace material relatively, sneak into tramp elements such as Cu and Ni in the steel that go out with electrosmelting and can not avoid.Think that this tramp element makes the rollforming deterioration.
The present invention is a purpose to address the above problem.That is, replace the blast furnace material to use the manufacturing of electric furnace material, prevent the rollforming deterioration with also producing effect, have the excellent quenching crack resistance and the machine structural steel product of torsional property simultaneously even purpose provides.In addition, provide the transmission shaft that uses these steel to form.
Summary of the invention
The inventor be achieve the above object and repeatedly the result of lucubrate obtain following opinion.
(1), increases the Cr amount effectively in order to alleviate the bad influence of tramp element;
(2), the increase of Cr amount causes with torsional property headed by the rollforming and machinability reduction;
(3) torsional property that accompanies with the increase of Cr amount and the reduction of machinability are eliminated by increasing the Si amount and reducing the Mn amount;
(4) reduction of rollforming is eliminated by the scope that will be controlled at defined as the LD value of the index of hardness that decides with hardening capacity and tissue;
The present invention is based on above-mentioned knowledge opinion and finishes.The certain content of invention is as follows.
1. the machine structural steel product of a rollforming, quenching crack resistance and torsional property excellence is characterized in that, be following composition: % represents with quality, and the scope that satisfies below 120 in the LD value with following formula (1) expression contains
More than the C:0.35%, below 0.50%,
Below the Si:0.15%,
More than the Mn:0.2%, below 1.1%,
Below the P:0.020%,
More than the S:0.005%, below 0.035%,
Cr: surpass below 0.1%, 0.2%,
More than the Mo:0.05%, below 0.5%,
More than the Ti:0.01 %, below 0.05%,
More than the Al:0.01%, below 0.05%,
Below the N:0.01%,
More than the B:0.0005%, below 0.0050%,
Reach more than the Cu:0.06%, below 0.25%
More than the Ni:0.05%, below 0.2%,
Remainder is Fe and unavoidable impurities,
LD＝0.569×{7.98×(C)
1/2×(1+4.1Mn)(1+2.83P)(1-0.62S)(1+0.64Si)
(1+2.33Cr)(1+0.52Ni)(1+3.14Mo)(1+0.27Cu)(1+1.5(0.9-C))}+52.6
---(1)
Wherein, the C in the formula, Mn, P, S, Si, Cr, Ni, Mo, Cu mean the content (quality %) of each element.
2. according to the machine structural steel product of above-mentioned the 1st described rollforming, quenching crack resistance and torsional property excellence, it is characterized in that steel are following composition: % represents with quality, also further contains
V:0.01% is above, below 0.30% and
More than the Nb:0.005%, below 0.050%.
3. a transmission shaft is characterized in that, adopts the described machine structural steel product of above-mentioned the 1st or the 2nd to form, thereby carries out high-frequency quenching, tempering is provided with cured layer.
The simple declaration of accompanying drawing
Fig. 1 is the figure of expression LD value to the influence of rollforming.
Fig. 2 is the result who measures the static strength of transmission shaft by static test of pressure.
Fig. 3 is the result by the fatigue strength of the transmission shaft of the transmission shaft of Stromeyer test mensuration example and comparative example.
Embodiment
Below specify the present invention.Illustrate that in the present invention the one-tenth with steel is grouped into the reason that is limited to above-mentioned scope.About " % " of composition expression only otherwise special declaration just means quality %.
More than the C:0.35%, below 0.50%
C is the element that has the greatest impact to high frequency hardening capacity, be the hardness and the degree of depth that improve the quenching cured layer, guarantee high-frequency quenching tempering retrotorsion intensity be more than the 1400MPa aspect useful element., its additive effect deficiency when containing quantity not sufficient 0.35% is caused machinability and quenching crack resistance reduction and surpass at 0.50% o'clock, therefore the C amount is limited to the scope more than 0.35%, below 0.50%.
Below the Si:0.15%
Si is except working, still strengthening the element that steel improves torsional strength by being solid-solubilized in as deoxidant element in the ferrite, preferred addition surpasses 0.05%., when the Si amount surpasses 0.15%, make the remarkable deterioration of machinability, therefore be limited to the scope below 0.15%.
More than the Mn:0.2%, below 1.1%
Mn improves the useful element that hardening capacity, the hardness depth when deepening high-frequency quenching help to improve torsional strength., its additive effect deficiency when containing quantity not sufficient 0.2%, and surpass at 1.1% o'clock, not only the rollforming deterioration also makes machinability and torsional strength deterioration, therefore the Mn amount is limited to the scope more than 0.2%, below 1.1%.Be preferably the scope more than 0.2%, below 0.8%.
Below the P:0.020%
P segregation when quenching encourages quenching crack and takes place in austenite grain boundary, therefore preferably does one's utmost to reduce, and from this viewpoint, regulation is suppressed at below 0.020%.
More than the S:0.005%, below 0.035%
S has the effect that forms MnS and improve machinability in steel, and therefore regulation contains more than 0.005%., MnS easily becomes the starting point of be full of cracks, cause intensity, toughness reduction, so the upper limit of S amount is limited to 0.035%.Be preferably the scope more than 0.010%, below 0.035%.
Cr: surpass 0.1%, below 0.2%
Cr is the element of particularly important in the present invention, by containing Cr, can be beneficial to the bad influence of eliminating tramp elements such as causing Cu that rollforming and torsional property, machinability etc. reduce and Ni., Cr amount is 0.1% when following, lacks its additive effect, and surpasses at 0.2% o'clock, and rollforming, machinability and torsional strength reduce, and therefore are defined in above the scope below 0.1%, 0.2% and contain Cr.
More than the Mo:0.05%, below 0.5%
Mo is not only useful to improving hardening capacity, also promotes bainite to generate, and the effect that improves machinability is arranged., need contain more than 0.05%, but content surpasses at 0.5% o'clock, causes the machinability deterioration for this reason, therefore the Mo amount is limited to the scope more than 0.05 %, below 0.5%.The scope more than 0.1%, below 0.5% preferably.
More than the Ti:0.01%, below 0.05%
Ti combines with N and forms nitride, the austenite crystal during the miniaturization heat.Be for guaranteeing to improving the useful essential element of solid solution B of hardening capacity., need contain more than 0.01% for this reason, but surpass 0.05% o'clock infringement toughness, therefore the Ti amount is limited to the scope more than 0.01%, below 0.05%.
More than the Al:0.01%, below 0.05%
Therefore Al need contain 0.01% at least as reductor and useful, but surpasses at 0.05% o'clock, generates thick aluminum oxide, and it becomes the starting point of fatigure failure, reduces fatigue strength, therefore Al is measured the scope that is limited to more than 0.01%, below 0.05%.
Below the N:0.01%
N forms nitride by combining with Al or Ti, the austenite crystal during the refinement heat, thereby the useful element of raising fatigue strength.Content surpasses at 0.01% o'clock, and the nitride alligatoring is instead make the fatigue strength deterioration.In addition, superfluous N adds and forms BN, also has to make the unfavorable aspect that the effective solid solution B amount of hardening capacity is reduced.Therefore the N amount is limited to below 0.01%.
More than the B:0.0005%, below 0.0050%
B improves hardening capacity, and the depth of hardening when improving high-frequency quenching has the effect that improves torsional strength thus.For this reason, need to add more than 0.0005%, cause the toughness deterioration, therefore B is limited to the scope more than 0.0005%, below 0.0050% but surpass at 0.0050% o'clock.
More than the Cu:0.06%, below 0.25%
Cu is the element of sneaking into inevitably as tramp element.When content surpasses 0.25%, cause deteriorations such as rollforming, therefore be decided to be below 0.25%.And be reduced to less than 0.06% o'clock, manufacturing cost increases, and therefore is defined as more than 0.06%.
More than the Ni:0.05%, below 0.2%
Ni is the element of sneaking into inevitably as tramp element.When content surpasses 0.2%, cause deteriorations such as rollforming, therefore be decided to be below 0.2%.And be reduced to less than 0.05% o'clock, manufacturing cost increases, and therefore is defined as more than 0.05%.
Basal component more than has been described, but in addition the present invention can suit as the element of following narration also.
More than the V:0.01%, below 0.30%, more than the Nb:0.005%, below 0.050%
V and Nb all form carbonitride, make the austenite crystal miniaturization, help to improve intensity effectively.; when V, Nb amount be respectively less than 0.01%, less than 0.005% the time; lack its additive effect; and be respectively surpass 0.30%, above 0.050% o'clock; the precipitate alligatoring; infringement toughness, therefore be each defined in V:0.01% above, 0.30% below, more than the Nb:0.005%, the scope below 0.050%.
Suitable composition compositing range more than has been described, but in the present invention, it is inadequate that each composition only only satisfies above-mentioned compositing range, is necessary to carry out the composition adjustment and reaches below 120 with the LD value of using following formula (1) expression.
LD＝0.569×{7.98×(C)
1/2×(1+4.1Mn)(1+2.83P)(1-0.62S)(1+0.64Si)
(1+2.33Cr)(1+0.52Ni)(1+3.14Mo)(1+0.27Cu)(1+1.5(0.9-C))}+52.6
---(1)
Wherein, the C in the formula, Mn, P, S, Si, Cr, Ni, Mo, Cu mean the content (quality %) of each element.
This LD value is to decide the index of hardness and tissue by hardening capacity.
Demonstrate the result of the above-mentioned LD value of investigation about high Cr of the present invention, high Si steel among Fig. 1 to the influence of rollforming.In addition, among this figure, in order to demonstrate the low Cr about record in the above-mentioned patent documentation 2, the investigation result of low Si steel more in the lump.
It should be noted, with estimating rollforming the die life in the rolling test.
As shown in the drawing, when any occasion LD value all surpassed 120, sharply reduced die life, but the LD value is a rollforming in the die life of the scope below 120, and high Cr of the present invention, high Si steel are very excellent.
Therefore, the present invention has carried out the composition adjustment so that above-mentioned LD value is below 120.
In the present invention, structure of steel is not particularly limited, but is preferably based on ferrite, contains the tissue of the bainite phase about area occupation ratio 5-30%.
Above Shuo Ming steel of the present invention, being used for power-transmitting part, especially automobile is best with transmission shaft and constant velocity cardan joint.Excellent in workability much less because loading capacity increases, therefore obtaining can this big effect of weight reduction.
Secondly, illustrate and of the present inventionly preferably create conditions.
The smelting process of steel of the present invention gets final product according to the ordinary method manufacturing, does not limit especially.Steel for mechanical structure provided by the invention even contain Cu and the Ni that is difficult to remove when using electrosmelting, also has good rollforming, therefore is particularly suitable for adopting electrosmelting.Also can add the degassing of RH degassing equal vacuum, refining etc. in hot metal ladle.Molten steel solidifies with continuous metal cast process or ingot casting method, after solidifying, makes via warm forging in hot rolling or the hot rolling, makes the base material of regulation shape.These base materials are implemented intermediate heat treatment such as normalizing, Spheroidizing Annealing, softening annealing as required, are finish-machined to desired shape by cold working such as cutting, forging, rollings.
In the present invention, implement hot rolling or forge hot or further normalizing treatment, and be finish-machined to article shape.After this hot rolling or the forge hot and then the cooling behind the austenitizing of normalizing etc., in order to generate the bainite of appropriate amount, preferably about 0.2-2.0 ℃/s.Particularly the bar steel of particle size is preferably and has adjusted refrigerative acceleration cooling.
In addition, the hardening apparatus by high frequency current about 15kHz is used in final high-frequency quenching tempering, in output rating: after implementing the heating of 0.2-1.0 about second down about 120kW, quench, get final product 170 ℃ of tempering of implementing about 30 minutes down.
Embodiment
With the steel that the one-tenth shown in the converter melting table 1 is grouped into, make the steel ingot of 400 * 540mm by continuous casting after, make the square billet of 150mm by hot rolling.After then this billet being heated to 1030 ℃, make the straight rod of Ф 25mm by hot rolling after, with 0.7 ℃/s of speed of cooling air cooling.
Table 2 is expressed the result who investigates about the tissue of the bar steel that obtains like this, rollforming, torsional property and quenching crack resistance.
The tissue of steel and the evaluation method of each characteristic are as follows.
(1) tissue
About cooled straight rod, adopt opticmicroscope to take microstructure, when resolving the tissue of steel, utilize visual resolver to measure the area occupation ratio of bainite phase from this photo.
(2) rollforming
With estimating rollforming the die life in the rolling test.With can rolling up to because the hypodontia of mould, the broken skin in surface are peeled off, to such an extent as to the number of the material till can not rolling such as odontotripsis is estimated this die life.
Mold material is SKD11, and the tooth bar data are as follows.
Profile of tooth: involute urve shape, modulus: 1.27, pressure angle: 30o, the number of teeth: 21, pitch diameters: 26.27mm, big footpath: 28.1mm, path: 24.88mm, roller diameter (Ф 2.5mm sells (pin)): 30.49mm
(3) torsional property
Make parallel portion from straight rod: the level and smooth pole twisting test sheet of Ф 20mm, the hardening apparatus by high frequency current of frequency of utilization: 15kHz quenches to it, implement 170 ℃, 30 minutes temper after, carry out twisting test.Full hardening deepness after the high-frequency quenching tempering is decided to be about 4mm.Twisting test uses the torsion testing machine of 4900J (500kgfm) to obtain the maximum twist shearing resistance, with it as torsional strength.
(4) quenching crack resistance
Quenching crack resistance has the pole (Ф 20mm) of axial V word groove from the straight excellent finished surface of above-mentioned Ф 25mm, carry out with above-mentioned (3) same high-frequency quenching after, 10 positions, C cross section of pole are observed in polishing, with its crackle generation number evaluation.
(5) machinability
The drill bit of SKH4, Ф 4mm is used in machinability test, carries out the long perforation of 12mm under the condition of rotating speed: 1500rpm, obtains the total perforate long (mm) till can not cutting, with it as estimating life tools.
Know clearly that by table 2 steel that obtain according to the present invention all have excellent rollforming, torsional property, quenching crack resistance and machinability.
About using steel of the present invention to form, carry out that high-frequency quenching, tempering are provided with cured layer and the static strength and the fatigue strength of the transmission shaft made, respectively with reference to Fig. 2, Fig. 3 explanation.The transmission shaft of example uses the No.2 steel of table 1 to make.The transmission shaft of comparative example uses the No.18 steel of table 1 to make.Fig. 2 is the result who measures the static strength of transmission shaft by static test of pressure.So-called static test of pressure (static strength test) is the peak torque when measuring transmission shaft destruction, estimates the test of static strength.For the transmission shaft radical of test, comparative example is 1, and example is 2.Among Fig. 2, be expressed as comparative example, example 1, example 2 respectively.The peak torque that acts on during with the drive shafts fracture of comparative example is designated as 1, uses the peak torque that acts on when representing the drive shafts fracture of example with its ratio.With respect to the transmission shaft of comparative example, the transmission shaft of example improves as can be known
About 1.17 times of static strength.
Fig. 3 is the result by the fatigue strength of the transmission shaft of the transmission shaft of Stromeyer test mensuration example and comparative example.So-called Stromeyer test (fatigue strengthtest) is the test of the fatigue strength when measuring the repeated load moment of torsion.Give the load torque of defined repeatedly to transmission shaft, the load of obtaining till fracture is counted N repeatedly.Ordinate zou is the value that load torque gets divided by the static strength of the transmission shaft of comparative example, is zero dimension.X-coordinate is the number of occurrence of the load of transmission shaft till fracture.Know that from this test-results for example the number of occurrence is 10000 times a occasion, the ordinate value of the transmission shaft of comparative example is about 0.49, and the ordinate value of the transmission shaft of example is about 0.55, and the fatigue strength of the transmission shaft of example improves about 10%.
Industrial applicibility
According to the present invention, can eliminate the bad influence of tramp element from the machine structural steel product that the electric furnace that uses tramp elements such as Cu and Ni to sneak into is inevitably made.Can access steel with excellent rollforming, torsional property, quenching crack resistance and hardening capacity.Steel of the present invention, by adopting in transmission shaft and constant velocity cardan joint at power-transmitting part, especially automobile, much less excellent in workability owing to be high strength, but so can access this big effect of weight reduction.
Table 1
| No. | Become to be grouped into (quality %) | The LD value | ||||||||||||||
| C | Si | Mn | P | S | Cu | Ni | Cr | Mo | Al | Ti | B | N | V | Nb | ||
| 2 | 0.40 | 0.08 | 0.45 | 0.013 | 0.018 | 0.16 | 0.16 | 0.16 | 0.17 | 0.032 | 0.019 | 0.0022 | 0.0044 | - | - | 89.3 |
| 3 | 0.39 | 0.08 | 0.25 | 0.011 | 0.020 | 0.16 | 0.15 | 0.15 | 0.16 | 0.040 | 0.020 | 0.0020 | 0.0038 | - | - | 77.3 |
| 5 | 0.42 | 0.10 | 0.65 | 0.013 | 0.020 | 0.11 | 0.10 | 0.11 | 0.25 | 0.025 | 0.015 | 0.0023 | 0.0041 | 0.11 | - | 101.7 |
| 6 | 0.40 | 0.08 | 0.95 | 0.016 | 0.015 | 0.16 | 0.16 | 0.16 | 0.12 | 0.023 | 0.024 | 0.0022 | 0.0045 | - | 0.020 | 109.8 |
| 7 | 0.41 | 0.06 | 0.70 | 0.019 | 0.006 | 0.11 | 0.12 | 0.12 | 0.36 | 0.026 | 0.019 | 0.0019 | 0.0048 | - | - | 116.1 |
| 8 | 0.40 | 0.08 | 0.60 | 0.019 | 0.007 | 0.22 | 0.16 | 0.16 | 0.35 | 0.026 | 0.025 | 0.0020 | 0.0052 | - | - | 116.0 |
| 10 | 0.41 | 0.07 | 0.60 | 0.016 | 0.015 | 0.11 | 0.10 | 0.12 | 0.15 | 0.023 | 0.024 | 0.0022 | 0.0045 | 0.15 | 0.032 | 91.1 |
| 11 | 0.40 | 0.06 | 0.84 | 0.018 | 0.007 | 0.11 | 0.11 | 0.11 | 0.35 | 0.025 | 0.023 | 0.0020 | 0.0041 | - | - | 122.2 |
| 12 | 0.41 | 0.08 | 0.73 | 0.019 | 0.007 | 0.16 | 0.16 | 0.15 | 0.34 | 0.023 | 0.024 | 0.0023 | 0.0047 | - | - | 122.5 |
| 13 | 0.42 | 0.04 | 0.99 | 0.018 | 0.006 | 0.06 | 0.06 | 0.06 | 0.35 | 0.024 | 0.021 | 0.0018 | 0.0045 | - | - | 121.5 |
| 14 | 0.61 | 0.06 | 0.63 | 0.012 | 0.021 | 0.13 | 0.12 | 0.13 | 0.16 | 0.022 | 0.019 | 0.0019 | 0.0054 | - | - | 94.2 |
| 15 | 0.31 | 0.08 | 0.57 | 0.011 | 0.020 | 0.15 | 0.16 | 0.13 | 0.17 | 0.031 | 0.020 | 0.0018 | 0.0060 | - | - | 90.9 |
| 16 | 0.40 | 0.04 | 1.22 | 0.014 | 0.023 | 0.16 | 0.15 | 0.17 | 0.26 | 0.034 | 0.017 | 0.0018 | 0.0065 | - | - | 143.0 |
| 17 | 0.42 | 0.23 | 0.70 | 0.025 | 0.024 | 0.14 | 0.11 | 0.10 | 0.16 | 0.025 | 0.024 | 0.0016 | 0.0056 | - | - | 100.8 |
| 18 | 0.39 | 0.04 | 0.54 | 0.014 | 0.045 | 0.32 | 0.26 | 0.26 | 0.15 | 0.022 | 0.023 | 0.0022 | 0.0048 | - | - | 101.2 |
| 19 | 0.40 | 0.05 | 0.48 | 0.014 | 0.020 | 0.11 | 0.10 | 0.11 | 0.62 | 0.024 | 0.020 | 0.0025 | 0.0046 | - | - | 116.0 |
| 20 | 0.38 | 0.05 | 0.52 | 0.013 | 0.018 | 0.11 | 0.11 | 0.09 | 0.03 | 0.025 | 0.022 | 0.0017 | 0.0049 | - | - | 76.4 |
| 21 | 0.37 | 0.02 | 1.00 | 0.015 | 0.030 | 0.08 | 0.05 | 0.03 | 0.35 | 0.021 | 0.023 | 0.0032 | 0.0052 | - | - | 114.3 |
Table 2
| No. | Tissue * | Bainite ratio (%) | Die life (individual) | Torsional strength (MPa) | Hardening crack number (individual) | Life tools (mm) | Remarks | ||
| 1 | F+P+B | 12 | 610 | 1540 | 15 | 2430 | Example | ||
| 2 | F+P+B | 14 | 624 | 1580 | 16 | 2480 | ″ | ||
| 3 | F+P+B | 10 | 642 | 1570 | 10 | 2300 | ″ | ||
| 4 | F+P+B | 13 | 588 | 1630 | 19 | 2390 | ″ | ||
| 5 | F+P+B | 18 | 591 | 1590 | 18 | 1740 | ″ | ||
| 6 | F+P+B | 8 | 525 | 1570 | 18 | 2110 | ″ | ||
| 7 | F+P+B | 23 | 493 | 1580 | 19 | 2470 | ″ | ||
| 8 | F+P+B | 21 | 469 | 1590 | 19 | 2450 | ″ | ||
| 9 | F+P+B | 20 | 512 | 1580 | 20 | 2440 | ″ | ||
| 10 | F+P+B | 10 | 658 | 1620 | 16 | 2120 | ″ | ||
| 11 | F+P+B | 21 | 253 | 1590 | 18 | 2300 | Comparative example | ||
| 12 | F+P+B | 19 | 218 | 1580 | 19 | 2320 | ″ | ||
| 13 | F+P+B | 22 | 226 | 1600 | 21 | 2310 | ″ | ||
| 14 | F+P+B | 11 | 599 | 1650 | 45 | 1120 | ″ | ||
| 15 | F+P+B | 7 | 635 | 1190 | 4 | 2130 | ″ | ||
| 16 | F+P+B | 14 | 151 | 1430 | 19 | 1940 | ″ | ||
| 17 | F+P+B | 17 | 585 | 1560 | 24 | 1290 | ″ | ||
| 18 | F+P+B | 16 | 523 | 1400 | 17 | 1270 | ″ | ||
| 19 | F+P+B | 45 | 514 | 1600 | 16 | 1510 | ″ | ||
| 20 | F+P | 0 | 663 | 1550 | 11 | 1330 | ″ | ||
| 21 | F+P+B | 26 | 360 | 1530 | 17 | 2400 | ″ | ||
* F: ferrite, P: perlite, B: bainite
Claims (3)
1. the machine structural steel product of a rollforming, quenching crack resistance and torsional property excellence is characterized in that, be following composition: % represents with quality, is that scope below 120 contains satisfying the LD value of representing with following formula (1),
More than the C:0.35%, below 0.50%,
Below the Si:0.15%,
More than the Mn:0.2%, below 1.1%,
Below the P:0.020%,
More than the S:0.005%, below 0.035%,
Cr: surpass 0.1%, below 0.2%,
More than the Mo:0.05%, below 0.5%,
More than the Ti:0.01%, below 0.05%,
More than the Al:0.01%, below 0.05%,
Below the N:0.01%,
More than the B:0.0005%, below 0.0050%,
Reach more than the Cu:0.06%, below 0.25%
More than the Ni:0.05%, below 0.2%, remainder is Fe and unavoidable impurities, LD=0.569 * { 7.98 * (C)
1/2* (1+4.1Mn) (1+2.83P) (1-0.62S) (1+0.64Si)
(1+2.33Cr)(1+0.52Ni)(1+3.14Mo)(1+0.27Cu)(1+1.5(0.9-C))}+52.6
---(1)
Wherein, the C in the formula, Mn, P, S, Si, Cr, Ni, Mo, Cu refer to the content (quality %) of each element.
2. the machine structural steel product of rollforming according to claim 1, quenching crack resistance and torsional property excellence is characterized in that, be following composition: % represents with quality, and steel also further contain,
Reach more than the V:0.01%, below 0.30%
More than the Nb:0.005%, below 0.050%.
3. a transmission shaft is characterized in that, adopts claim 1 or 2 described machine structural steel products to form, thereby carries out high-frequency quenching, tempering is provided with cured layer.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP304190/2002 | 2002-10-18 | ||
| JP2002304190 | 2002-10-18 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1688733A CN1688733A (en) | 2005-10-26 |
| CN1307319C true CN1307319C (en) | 2007-03-28 |
Family
ID=32105100
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB028297733A Expired - Fee Related CN1307319C (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 |
Country Status (7)
| Country | Link |
|---|---|
| US (1) | US20060065328A1 (en) |
| EP (1) | EP1553197B1 (en) |
| JP (1) | JP4170294B2 (en) |
| CN (1) | CN1307319C (en) |
| DE (1) | DE60222595T2 (en) |
| ES (1) | ES2292836T3 (en) |
| WO (1) | WO2004035848A1 (en) |
Families Citing this family (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| SE527221C2 (en) * | 2005-04-12 | 2006-01-24 | Scania Cv Abp | Drilling steel for induction hardening, has low alloy composition containing silicon, manganese, phosphorous, sulphur, chromium, molybdenum, nickel, titanium, aluminium and boron |
| JP2007154305A (en) * | 2005-07-05 | 2007-06-21 | Jfe Steel Kk | Steel for mechanical structure with excellent strength, ductility and toughness, and its manufacturing method |
| MY196779A (en) * | 2017-05-18 | 2023-05-03 | Nippon Steel Corp | Wire rod, drawn steel wire, and method for manufacturing drawn steel wire |
| WO2020179800A1 (en) * | 2019-03-05 | 2020-09-10 | 日本製鉄株式会社 | Crankshaft |
| JP7485234B1 (en) | 2022-06-24 | 2024-05-16 | Ｊｆｅスチール株式会社 | High-frequency hardening steel |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4702778A (en) * | 1985-01-28 | 1987-10-27 | Nippon Steel Corporation | Method for softening rolled medium carbon machine structural steels |
| JPH093592A (en) * | 1995-06-19 | 1997-01-07 | Toa Steel Co Ltd | Steel for machine structure excellent in cold workability and high induction hardenability |
| JPH0920958A (en) * | 1995-06-30 | 1997-01-21 | Nkk Corp | Hot rolled steel sheet for press forming excellent in secondary working resistance and its production |
| CN1163942A (en) * | 1996-02-08 | 1997-11-05 | 阿斯克迈塔尔公司 | Steel for manufacture of forging and process for manufacturing forging |
Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| 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 (en) * | 1990-05-02 | 2000-07-10 | 川崎製鉄株式会社 | Steel for high strength shaft parts |
| JP3288563B2 (en) * | 1995-10-17 | 2002-06-04 | 川崎製鉄株式会社 | Steel for mechanical structure excellent in machinability and resistance to fire cracking and method for producing the same |
| JP3402562B2 (en) * | 1996-07-19 | 2003-05-06 | 大同特殊鋼株式会社 | Induction hardened parts |
| WO1999005333A1 (en) * | 1997-07-22 | 1999-02-04 | Nippon Steel Corporation | Case hardened steel excellent in the prevention of coarsening of particles during carburizing thereof, method of manufacturing the same, and raw shaped material for carburized parts |
| JP2000154828A (en) * | 1998-11-19 | 2000-06-06 | Nippon Steel Corp | Outer ring for constant velocity universal joint excellent in anti-flaking characteristic and shaft strength and manufacture thereof |
-
2002
- 2002-12-26 DE DE60222595T patent/DE60222595T2/en not_active Expired - Lifetime
- 2002-12-26 WO PCT/JP2002/013564 patent/WO2004035848A1/en active IP Right Grant
- 2002-12-26 US US10/526,802 patent/US20060065328A1/en not_active Abandoned
- 2002-12-26 EP EP02790877A patent/EP1553197B1/en not_active Expired - Lifetime
- 2002-12-26 JP JP2004544722A patent/JP4170294B2/en not_active Expired - Lifetime
- 2002-12-26 CN CNB028297733A patent/CN1307319C/en not_active Expired - Fee Related
- 2002-12-26 ES ES02790877T patent/ES2292836T3/en not_active Expired - Lifetime
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4702778A (en) * | 1985-01-28 | 1987-10-27 | Nippon Steel Corporation | Method for softening rolled medium carbon machine structural steels |
| JPH093592A (en) * | 1995-06-19 | 1997-01-07 | Toa Steel Co Ltd | Steel for machine structure excellent in cold workability and high induction hardenability |
| JPH0920958A (en) * | 1995-06-30 | 1997-01-21 | Nkk Corp | Hot rolled steel sheet for press forming excellent in secondary working resistance and its production |
| CN1163942A (en) * | 1996-02-08 | 1997-11-05 | 阿斯克迈塔尔公司 | Steel for manufacture of forging and process for manufacturing forging |
Also Published As
| Publication number | Publication date |
|---|---|
| EP1553197A1 (en) | 2005-07-13 |
| DE60222595D1 (en) | 2007-10-31 |
| WO2004035848A1 (en) | 2004-04-29 |
| US20060065328A1 (en) | 2006-03-30 |
| JP4170294B2 (en) | 2008-10-22 |
| JPWO2004035848A1 (en) | 2006-02-16 |
| EP1553197B1 (en) | 2007-09-19 |
| ES2292836T3 (en) | 2008-03-16 |
| DE60222595T2 (en) | 2008-06-19 |
| CN1688733A (en) | 2005-10-26 |
| EP1553197A4 (en) | 2006-07-05 |
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