CN104099535A - Surface carburizing steel with excellent cold forging performance and low-carburizing deformation characteristic - Google Patents
Surface carburizing steel with excellent cold forging performance and low-carburizing deformation characteristic Download PDFInfo
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Abstract
The invention provides surface carburizing steel having low deformation resistance and high limit compression ratio at the low temperature so as to obtain excellent cold forging performance and low carburizing deformation; and the surface carburizing steel with excellent cold forging performance and low-carburizing deformation characteristic is characterized by comprising the following raw materials in percentage by mass: 0.07-0.3% of C, 0.01-0.15% of Si, 0.1-0.7% of Mn, P below 0.03%, 0.002-0.10% of S, 0.01-0.08% of Al, 0.7-1.5% of Cr, 0.01-0.15% of Ti, 0.0005-0.005% of B, N below 0.008%, and the balance of Fe and inevitable impurities; more than 65% of metal structure is a ferritic phase; and a bainite phase is low 15%.
Description
The application is to be that September 28, Chinese application number in 2007 are 200710153141.7 and the divisional application of the denomination of invention patent application that is " case hardening steel of forging and low carburizing excellent in deformation characteristics " the applying date.
Technical field
The present invention relates to the case hardening steel of forging and low carburizing excellent in deformation characteristics.
Background technology
At the steel for mechanical structured members such as gear and axle, CVJ spare and accessory parts, conventionally use the case hardening steel that has added Cr and Mo.Become after predetermined shape by cold forging-machining, adopt the operation of carrying out carburizing and quenching to make.Cold forging is because epidermis, the dimensional precision of product are good, and manufacturing cost is lower compared with forge hot, yield rate is also good, so the spare and accessory parts that adopted in the past forge hot to make are transferred to and adopt the tendency that cold forging is manufactured to strengthen, adopt the object of the carburizing spare and accessory parts of cold forging-carburization step making obviously to increase in recent years.At this, at the Turning Point from forge hot to cold forging, the reduction of steel cold deformation resistance and the raising of limit rate of compression become important problem.This be because: the former will guarantee the life-span of forging tools, the cracking of the latter's steel when preventing cold forging.
Based on such object, for example JP 2001-329339 communique discloses the invention of a kind of cold forging case hardening steel, by C amount is controlled to 0.1～0.4% scope, and controls the shape that B is inclusion, thereby has improved forging.Unexamined Patent 11-335777 communique and JP 2001-303172 communique disclose the invention of another kind of cold forging case hardening steel, in 0.1～0.3% C content range, reduce Si and Mn amount, and guarantee hardening capacity by adding B, and then reduce bainite mark, make thus forging be improved.
Summary of the invention
But, in invention up to now, although the gear of can the cold forging shape less simple shape such as gear and horizontal gear, but in the time of the spare and accessory parts of the large complicated shape such as spare and accessory parts and spiral wheel of cold forging, the cracking of steel will be there is, the angle consideration of the limit rate of compression during from forging, this is still sufficient not.In addition, although further require to reduce recently the noise of automobile, must reduce the gear noise that becomes its major cause, in invention up to now, the reduction of carburizing distortion is sufficient not.Problem of the present invention is: a kind of steel are provided, in the resistance to deformation in the time reducing cold forging steel, also to improve significantly limit rate of compression compared with former steel, thus in the cold forging of the spare and accessory parts of large spare and accessory parts and complicated shape, the cold forging excellent property that crackle does not occur, and distortion when carburizing is also less.
For improving the cold-workability of case hardening steel, first present inventor has carried out various tests with regard to the method that reduces resistance to deformation, thereby has obtained following opinion: it is very important reducing Si and Mn.
Secondly also obtained following opinion: for the method not rising with resistance to deformation makes up the reduction because reducing the hardening capacity that these elements cause, the interpolation of B and Cr is effective.
Again also obtain following opinion: for improving limit rate of compression, finding, only according to reducing resistance to deformation, sometimes may not realize, is very important and improve ferrite mark.
Moreover, find, by improving ferrite mark, can reduce the distortion of carburizing and quenching, thereby the present invention is accomplished.
, main points of the present invention are as follows:
(1) case hardening steel for forging and low carburizing excellent in deformation characteristics, is characterized in that: in quality %, contain:
C：0.07～0.3％
Si：0.01～0.15％
Mn：0.1～0.7％
Below P:0.03%
S：0.002～0.10％
A1：0.01～0.08％
Cr：0.7～1.5％
Ti：0.01～0.15％
B：0.0005～0.005％
Below N:0.008%, surplus is made up of Fe and inevitable impurity; Metal structure more than 65% be ferritic phase, Bainite Phases of Some is below 15%.
(2) according to the forging above-mentioned (1) Suo Shu and the case hardening steel of low carburizing excellent in deformation characteristics, it is characterized in that: in quality %, further contain Mo:0.005～0.3%, among Ni:0.1～4.5% a kind or 2 kinds.
According to the present invention, can provide a kind of converted steel, in the time of the spare and accessory parts of cold forging complicated shape, its resistance to deformation is low, can not crack, and the distortion producing when carburizing and quenching is less, thereby can significantly reduce the manufacturing cost of spare and accessory parts, and increase substantially the form accuracy of spare and accessory parts.
Brief description of the drawings
Fig. 1 represents the relation between ferrite mark and the limit rate of compression of metal structure of rolling stock.
Fig. 2 represents the relation between speed of cooling and ferrite mark after finish rolling.
Fig. 3 represents the relation between hardness and the limit rate of compression of rolling stock.
Fig. 4 represents the relation between hardness and the resistance to deformation of rolling stock.
Fig. 5 represents the shape of deformation at room temperature drag measurement test film.
Fig. 6 represents the shape of limit rate of compression measurement test film.
Fig. 7 represents the relation between bainite mark and out of roundness.
Fig. 8 represents the relation between ferrite mark and out of roundness.
Embodiment
The opinion of the present invention based on above-mentioned and completing, about for obtain forging and low carburizing excellent in deformation characteristics case hardening steel become to be grouped into, in particular for reducing resistance to deformation, less add Si:0.01～0.15%, Mn:0.1～0.7%, and then for the rising that suppresses resistance to deformation improves hardening capacity simultaneously, more add Cr:0.7～1.5%, for improving hardening capacity and increasing ferrite mark etc., must add B:0.0005～0.005%; In addition, about metal structure, for realize the raising of limit rate of compression and the reduction of carburizing and quenching distortion simultaneously, after hot rolling, carry out cooling speed by restriction, just can make ferritic phase: be more than 65%, Bainite Phases of Some: be below 15%.
Just the present invention is described in detail below.
C：0.07～0.3％
C is effective element providing aspect the needed intensity of steel, but when less than 0.07%, can not guarantee needed tensile strength, hardening while exceeding 0.3%, thus forging is deteriorated, so C is set as 0.07～0.3%.Be preferably 0.07～0.25%.
Si：0.01～0.15％
Si is to the effective element of the deoxidation of steel, is also to provide the needed intensity of steel, hardening capacity simultaneously, improves the effective element of annealing softening resistance, but when less than 0.01%, its effect is sufficient not.On the other hand, while exceeding 0.15%, cause hardness to increase, thereby make forging deteriorated.Therefore, Si is set as 0.01～0.15%.
Mn：0.1～0.7％
Mn is to the effective element of the deoxidation of steel, is simultaneously also to provide the needed intensity of steel, the effective element of hardening capacity, but when less than 0.1%, its effect is abundant not, and in the time exceeding 0.7%, its effect not only reaches capacity, and cause the rising of hardness, so that forging occurs deteriorated.Therefore, Mn is set as 0.1～0.7%.The scope of preferred Mn is 0.1～0.6%.
Below P:0.03%
When P is a small amount of, be the element that improves the resistance to deformation of steel, should reduce as much as possible its content.Exceed the rising that 0.03% content causes hardness, so that forging occurs deteriorated.Therefore, P is limited in below 0.03%.
S：0.002～0.10％
S forms MnS in steel, and its object that rises to consequent machinability is added, but when less than 0.002%, its effect is sufficient not.On the other hand, when addition exceedes 0.10%, the crack sensitivity will improve cold forging time, thus limit rate of compression is minimized.Therefore, S is set as 0.002～0.10% scope.
Al：0.01～0.08％
Al adds as reductor.When less than 0.01%, its effect is sufficient not.On the other hand, in the time exceeding 0.08%, the inclusion of aluminum oxidation system increases, and the probability that becomes fatigure failure starting point increases, thereby it is deteriorated that forging is occurred.Therefore, Al is set as 0.01～0.08% scope.
Cr：0.7～1.5％
The influence power of the raising of the resistance to deformation of Cr when cold rolling is less, and is effectively to give the useful element of steel with hardening capacity.When less than 0.7%, the hardening capacity of giving spare and accessory parts is abundant not, on the other hand, when addition exceedes 1.5%, carburizing performance degradation.Therefore, the scope of Cr is set as 0.7～1.5%.Preferred interpolation scope is 0.9～1.5%.
B：0.0005～0.005％
B adds taking 3 following aspects as target.1. in the time of bar and rod rolling, generate ferro-boron carbide by the process of cooling after rolling, increase the ferritic speed of growth, thereby increase ferrite mark.2. solid solution B, in the time of carburizing and quenching, gives steel with hardening capacity.And can improve hardly resistance to deformation.3. solid solution B, by improving the grain-boundary strengthening of carburized material, improves fatigue strength and shock strength as carburizing spare and accessory parts.In the time of addition less than 0.0005%, above-mentioned effect is inadequate, and in the time exceeding 0.005%, its effect reaches capacity.Therefore, the interpolation scope of B is set as B:0.0005～0.005%.
Ti：0.01～0.15％
Ti generates TiN with N combination in steel, to fix solid solution N, prevents thus separating out of BN.Like this, can guarantee added solid solution B, the hardening capacity of performance B.In the time that Ti adds less than 0.01%, its effect is sufficient not.On the other hand, exceed 0.15% interpolation the effect of precipitation-hardening is increased, thus infringement forging.Therefore, Ti is set as 0.01～0.15%.
Below N:0.008%
As mentioned above, guarantee solid solution B in order not generate BN, must make solid solution N become TiN precipitate by adding Ti, but in the time that the N content in steel exceedes 0.008%, thick TiN increases, cracking while likely causing cold forging, or also become the starting point of fatigure failure.Therefore, N is limited in below 0.008%.Preferred scope is below 0.006%.
Mo：0.005～0.3％
The interpolation of Mo mainly brings 3 effects.The first improves the effect of the hardening capacity of steel.It two is by improving the softening resistance of temperature rise in using for spare and accessory parts, improves the effect of surface fatigue intensity.The 3rd is the crystal boundary of strengthening carburized material, thereby improves the effect of impact characteristics.When less than 0.005%, can not obtain fully these effects, on the other hand, in the time that addition exceedes 0.3%, the resistance to deformation of room temperature is improved, thereby it is deteriorated that forging is occurred.Therefore, the interpolation scope of Mo is set as 0.005～0.3%.
Ni：0.1～4.5％
The Ni adding mainly brings 2 effects.The first improves the effect of the hardening capacity of steel.It two is the effects of toughness that improve steel.When less than 0.1%, can not obtain fully these effects, on the other hand, when addition exceedes 4.5%, the resistance to deformation of room temperature is improved, thereby it is deteriorated that forging is occurred.Therefore, the interpolation scope of Ni is set as 0.1～4.5%.
Secondly more than 65% be just, that the necessity of ferritic phase describes as the metal structure of the most important technology of the present invention.
Dissolve and hot rolling is selected at C:0.07～0.8%, Si:0.01～0.15%, Mn:0.1～0.7%, below P:0.03%, in S:0.005～0.10%, Al:0.01～0.008%, Cr:0.7～1.5%, Ti:0.01～0.15%, B:0.0005～0.005%, scope below N:0.008%, surplus is by iron and various steel that become to be grouped into that inevitably impurity forms, and makes the bar of φ 60.At this moment, the temperature range of 800～500 DEG C after hot finishing system is changed with the speed of 0.1～1 DEG C/sec.
Made the test film of size as shown in Figure 5 by these bars, at room temperature measure resistance to deformation, obtain at the stress that is deformed at 0.5 o'clock.In addition, make test film as shown in Figure 6, at room temperature measured limit rate of compression.On the other hand, study the metal structure of the longitudinal section of the bar of each level, measured ferrite mark.In addition, also measured the HV hardness of this section.Again on the one hand, made the circular disc test specimen of φ 55 × thickness 15 by bar, carried out the carburizing treatment of 950 DEG C × 5 hours, from 850 DEG C of annealing of quenching, measured out of roundness.Out of roundness utilizes commercially available out of roundness instrument to measure according to JIS B0621-1984.
As shown in Figure 4, if reduce hardness, resistance to deformation will reduce, but as shown in Figure 3, even lower hardness, limit rate of compression also not necessarily reduces.But as shown in Figure 1, large if ferrite mark becomes, limit rate of compression improves, its effect 65% when above clearly.
As shown in Figure 2, be more than 65% for making ferrite mark, as long as just make speed of cooling after hot finishing be 0.3 DEG C/sec can to realize below.Such slow cooling is not to be placed on and in atmosphere, to carry out coolingly in rolling, but for example can take to use the method for covering bar etc. with the slow cooling lid of thermal source to carry out.
In addition, the reason that while increasing ferrite mark, limit rate of compression improves can be presumed as follows: in the time that ferrite mark increases, perlite mark reduces.It is generally acknowledged the starting point ftractureing when sheet globular cementite in perlite becomes cold forging.
Secondly, the relation between the out of roundness after ferrite mark and carburizing and quenching as shown in Figure 8.Can do following supposition about this phenomenon: in the time that ferrite mark is higher, perlite mark diminishes, but correspondingly the amount of the C in perlite increases, the thickening of lamella cementite., while heating in carburizing, just expend time in for fully dissolving thicker cementite for this reason, will change γ phase at higher temperature.The dislocation that cold forging is put aside, because high temperature just more easily recovers and merges disappearance, so recrystallize will finish before γ phase transformation, regenerates crystal grain.It is generally acknowledged that the coarsening of crystal grain is just suppressed by regenerating crystal grain.
Present inventor has obtained following neodoxy: in the time improving ferrite mark, distortion when carburizing and quenching also diminishes.As shown in Figure 8, ferrite mark is 65% when above, and the effect that distortion reduces is just larger.
According to above test-results, the ferrite mark after rolling is set as more than 65%.
Secondly, illustrate bainite mark is set as to the reason below 15%.
If sneak into bainite structure in the steel after hot rolling, the generation of coarse grain may cause carburizing heating time.The generation of coarse grain likely increases the distortion after carburizing and quenching, has carried out following test for this reason.
; dissolve and hot rolling at C:0.07～0.8%, Si:0.01～0.15%, Mn:0.1～0.7%, below P:0.03%, in S:0.005～0.10%, Al:0.01～0.08%, Cr:0.7～1.5%, Ti:0.01～0.15%, B:0.0005～0.005%, scope below N:0.008% the various steel that become to be grouped into that select, that surplus is made up of with inevitable impurity iron; the temperature range of 800～500 DEG C after hot finishing is changed with the speed of 0.1～3 DEG C/sec, thereby produce the bar of φ 60.At this, study the metal structure of the bar longitudinal section of each level, measure bainite mark.On the other hand, made the circular disc test specimen of φ 56 × thickness 15 by bar, carry out the carburizing treatment of 950 DEG C × 5 hours, from 850 DEG C of annealing of quenching, measured out of roundness.Out of roundness adopts commercially available out of roundness instrument to measure according to JIS B0621-1984.Result as shown in Figure 7.Hence one can see that, and in the time that bainite mark exceedes 15%, out of roundness enlarges markedly (the skew distortion from proper circle is larger).Therefore, bainite mark is set as below 15%.The inhibition of bainite mark considers it is also preferred from improving the angle of forging.
In addition, can be confirmed by above-mentioned test-results: be below 15% for making bainite mark, just can realize below by making speed of cooling after hot finishing system be 1 DEG C/sec.
Although steel of the present invention is the steel that cold forging performance is very good,, can certainly carry out forge hot and warm forging, steel of the present invention is the steel that can make with multiple such operation combinations spare and accessory parts.
Further describe the present invention below by embodiment, but these embodiment do not have the character of the present invention of restriction, carry out in being included in of design alteration technical scope of the present invention according to main idea above-mentioned, described later.
Embodiment 1
Dissolve steel as shown in table 1 and carry out hot rolling, to manufacture the bar of φ 55.At this, manufacture with the speed of cooling of 800～500 DEG C of temperature ranges after the hot finishing of various levels.The metal structure of the longitudinal section of the bar with nital after to hot rolling carries out etch, has carried out afterwards the observation based on opticmicroscope, thereby ferrite mark and bainite mark are measured.Deformation at room temperature drag measurement test film shown in shop drawings 5, has at room temperature measured resistance to deformation, to obtain the distortion stress of 0.5 o'clock.In addition, the limit rate of compression measurement test film shown in construction drawing 6, has at room temperature measured limit rate of compression.On the other hand, made the circular disc test specimen of φ 52 × thickness 15 by bar, carry out the carburizing treatment of 950 DEG C × 5 hours, from 850 DEG C of annealing of quenching, measured out of roundness.Out of roundness adopts commercially available out of roundness instrument to measure according to JIS B0621-1984.
Specimen coding 1 to 9 is inventive examples, all has good low resistance to deformation and good limit rate of compression.Specimen coding 10 to 19 is comparative examples.Specimen coding 10 is because Si has exceeded compared with high the example that the scope of the invention thereby resistance to deformation are increased.Specimen coding 11 is because Mn has exceeded compared with high the example that the scope of the invention thereby resistance to deformation are increased.Specimen coding 12 is because C has exceeded compared with high the example that the scope of the invention thereby resistance to deformation are increased.Specimen coding 13 be due to Ti compared with high exceeded the scope of the invention thereby resistance to deformation is increased, limit rate of compression reduce example.Specimen coding 14 is because N is compared with the high example that has exceeded the scope of the invention thereby generated thick TiN, the reduction of limit rate of compression.Specimen coding 15 is JIS SCr420, due to Si, Mn, Ti, B, the N content example that resistance to deformation is increased from the scope of the invention is different.Specimen coding 16 is JIS SCM420, due to Si, Mn, Ti, B, the N content example that resistance to deformation is increased from the scope of the invention is different.Specimen coding 17 is JISSNCM815, due to Si, Mn, Ti, B, the N content example that resistance to deformation is increased from the scope of the invention is different.Although specimen coding 18 compositions are within the scope of the invention, because ferrite mark departs from the scope of the invention, although thereby resistance to deformation lower, and there is deteriorated example in out of roundness after limit rate of compression and carburizing.Although specimen coding 19 compositions within the scope of the present invention, because ferrite mark and bainite mark depart from scope of the present invention, thereby there is deteriorated example in out of roundness after resistance to deformation, limit rate of compression and carburizing.
The composition (mass) of table 1 steel
Table 2
Claims (2)
1. a gear case hardening steel for forging and low carburizing excellent in deformation characteristics, is characterized in that: in quality %, contain:
C：0.07～0.3％、
Si：0.01～0.15％、
Mn：0.1～0.7％、
Below P:0.03%,
S：0.002～0.10％、
A1：0.01～0.08％、
Cr：1.00～1.5％、
Ti：0.01～0.15％、
B：0.0005～0.005％、
Below N:0.008%, surplus is made up of Fe and inevitable impurity; Metal structure is that ferritic phase is more than 65% and does not contain the ferrite-pearlite tissue of Bainite Phases of Some.
2. a gear case hardening steel for forging and low carburizing excellent in deformation characteristics, is characterized in that: in quality %, contain:
C：0.07～0.3％、
Si：0.01～0.15％、
Mn：0.1～0.7％、
Below P:0.03%,
S：0.002～0.10％、
A1：0.01～0.08％、
Cr：1.00～1.5％、
Ti：0.01～0.15％、
B：0.0005～0.005％、
Below N:0.008%,
And further contain a kind or 2 kinds among Mo:0.005～0.3%, Ni:0.1～4.5%, surplus is made up of Fe and inevitable impurity; Metal structure is that ferritic phase is more than 65% and does not contain the ferrite-pearlite tissue of Bainite Phases of Some.
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
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| JP2017133052A (en) * | 2016-01-26 | 2017-08-03 | 新日鐵住金株式会社 | Case hardened steel excellent in coarse particle prevention property, fatigue property and machinability during carburization and manufacturing method therefor |
| CN112981236A (en) * | 2021-01-27 | 2021-06-18 | 江阴兴澄特种钢铁有限公司 | Steel for inner raceway of constant velocity universal joint and production method thereof |
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| CN112981236A (en) * | 2021-01-27 | 2021-06-18 | 江阴兴澄特种钢铁有限公司 | Steel for inner raceway of constant velocity universal joint and production method thereof |
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