CN101210298A - Steel for high-speed cold working and method for production thereof, and high-speed cold working part and method for production thereof - Google Patents
Steel for high-speed cold working and method for production thereof, and high-speed cold working part and method for production thereof Download PDFInfo
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Abstract
Disclosed herein is a steel for high-speed cold working which exhibits good cold workability during working and also exhibits high hardness after working. The steel for high-speed cold working contains C : 0.03 to 0.6% (by mass), Si : 0.005 to 0.6%, Mn : 0.05 to 2%, P : no more than 0.05% (excluding 0%), S : no more than 0.05% (excluding 0%), and N : no more than 0.04% (excluding 0%), with the remainder being iron and inevitable impurities and the amount of dissolved nitrogen in the steel being no less than 0.006%.
Description
Technical field
The present invention relates to be used to make the mechanical component of bolt/nut etc., the used cold-working steel of part, particularly cold working that special automobile is used is with wire rod or bar steel.The present invention also provides the cold working part that is obtained by described cold-working steel.
Background technology
In recent years, from the viewpoint of environment protection, attempt to improve automobile etc. vehicle fuel efficiency and wish that the light-weighted hope of part improves.General high strength part is to add alloying element amount in the iron to by raising, thereby guarantees the intensity as part.
Cold working (referring to the processing under the atmosphere below 200 ℃ here) is processed with temperature with hot-work and is compared, and has the productivity height, and size is superior good, and therefore the good such advantage of the yield rate of steel is widely used in the manufacturing of various parts.In addition, in order further to improve productivity, also has the trend of High-speed machiningization.
Under such background, the resistance to deformation that the employed steel of cold working just need be when cold working is low, and the work in-process energy of deformation can not reduce.This is because if the resistance to deformation height of steel then causes the life-span of the metal pattern that uses and reduces in cold working, on the other hand, if energy of deformation is low, crackle takes place then easily during cold working.
For the resistance to deformation that makes steel reduces, and make energy of deformation improve the known interpolation element that can reduce C, Si, Mn etc.Yet, if merely reduce to add element and resistance to deformation reduced, though can improve the life-span of metal pattern, can be created in can not get after the processing need the such problem of part strength.Therefore, always after steel is cold worked into the regulation shape,, and implement the thermal treatment of Q-tempering etc. in order to ensure the part strength (hardness) of regulation.
Yet if implement thermal treatment after part processing, accessory size changes, the part processing that therefore must not no longer carry out being cut thereafter etc.In order to improve productivity and energy-conservation, in the part strength of guaranteeing to stipulate, also expect such as omitting thermal treatment and the such countermeasure of processing thereafter.
Under as above background, No. 3515923 communique of patent discloses the increase for the resistance to deformation in suppressing to process, and separates out fine nitride in the ferrite crystal grain and make, and is that nuclear is separated out the C compound of cementite etc. with it.
The spy opens clear 60-82618 communique and discloses the amount by control N and solid solution Al, and N is fixed as AlN, by ageing treatment C is separated out as the C compound again, thereby can suppress the age hardening that brings because of solid solution C and solid solution N.
In the method for No. 3515923 communique of above-mentioned patent and the clear 60-82618 communique of Te Kai, in order to suppress dynamic strain aging, suppressing the increase of resistance to deformation, and in ferrite crystal grain with solid solution N and solid solution C as N compound and C compound and in addition immobilization.For fixing solid solution N, need to add Al as N compound formation element.As embodiment, if Al is 0.039～0.045%, even think that then the N amount is 0.015%, solid solution N also exists hardly.In addition, because the N compound has the inhibition effect of precipitation strength and thickization of crystal grain, so think that the key element beyond the dynamic strain aging also can make resistance to deformation increase.
Special public clear 57-60416 communique discloses a kind of method, is to have the Cr of solid solution ramollescence and by the immobilization of adding the solid solution N that Al brings by interpolation, and the resistance to deformation when reducing cold working.Yet, in the method, because be that solid solution N is used as the N compound and immobilization by interpolation Al, thus the same with No. 3515923 communiques of patent with the clear 60-82618 communique of Te Kai, think that solid solution N exists hardly.In addition, the same with No. 3515923 communique of patent with the clear 60-82618 communique of Te Kai, because the N compound has the inhibition effect of precipitation strength and thickization of crystal grain, think that therefore the key element beyond the attitude strain aging also can make resistance to deformation increase.
Cold working part after the cold working in order to ensure the part strength of regulation, is handled though can carry out hardening heat, for example carries out Q-tempering, as above-mentioned, from improving productivity and energy-conservation viewpoint, then requires to omit the thermal treatment of Q-tempering.
For example, opening the spy and to disclose a kind of method in the 2003-266144 communique, is by cooling off with the speed of cooling of 50～70 ℃/hr heating temp to the normal temperature after to cold working, and (Q-tempering) handled in the age hardening that can omit thus after the cold working.
Part strength after cold-workability (resistance to deformation and energy of deformation) and the cold working has opposite character.As if the part strength of guaranteeing to stipulate, then crackle takes place in metal pattern life-span deterioration easily in the processing.On the other hand, if improve the metal pattern life-span and cold-workability improved, then can not guarantee the part strength of stipulating.Can't obtain the cold-working steel of the non-quenching and tempering type of the good coexistence of this two specific character in the past always.
Summary of the invention
Therefore, the objective of the invention is to, a kind of good part strength that demonstrates after processing is provided, excellent cold-working steel, particularly cold working of its cold-workability of work in-process is with wire rod or bar steel on the other hand.
Can reach the steel for high-speed cold working of the basic mode of the present invention of above-mentioned purpose, it contains:
C:0.03%～0.6% (meaning of quality %, down together),
Si：0.005～0.6％、
Mn：0.05～2％、
P:0.05% following (not containing 0%),
S:0.05% following (not containing 0%),
N:0.04% following (not containing 0%), surplus is iron and unavoidable impurities, the solid solution nitrogen amount in the steel is more than 0.006%.
According to the performance of purposes and requirement, also the C content of steel for high-speed cold working of the present invention further can be limited to 0.03～0.15% (first embodiment of the present invention) or 0.15～0.6% but do not comprise 0.15% (second embodiment of the invention).
In basic mode of the present invention, in first and second embodiments,, guarantees solid solution N, more than the preferred N:0.007% more than 0.006% for being measured.
In basic mode of the present invention, in first and second embodiments, except mentioned component, it is also effective to contain Al:0.1% following (not containing 0%) as required again.
In basic mode of the present invention, in first and second embodiments, except mentioned component, it is also effective also to contain at least a kind of selecting the group who constitutes from following element as required: (do not contain 0%) below the Zr:0.2%, (do not contain 0%) below the Ti:0.1%, (do not contain 0%) below the Nb:0.1%, (do not contain 0%) below the V:0.5%, (do not contain 0%) below the Ta:0.1% and (do not contain 0%) below the Hf:0.1%.
In basic mode of the present invention, in first and second embodiments, except mentioned component, it is also effective also to contain at least a kind of selecting the group who constitutes from following element as required: (do not contain 0%) below the B:0.0015% and/or (do not contain 0%) below the Cr:2%.
At this moment, recommend above-mentioned each composition to satisfy following formula (1).
[N]-(14[Al]/27+14[Ti]/47.9+14[Nb]/92.9+14[V]/50.9+14[Zr]/91.2+14[B]/10.8+14[Ta]/180.9+14[Hf]/178.5) 〉=0.006 ... (1) formula
[[] represents the total content (quality %) of each element in steel in the formula (1)]
As one of equally preferred embodiment (the 3rd embodiment of the present invention), the content of described unavoidable impurities satisfies in addition:
Al:0.001% following (containing 0%),
Ti:0.002% following (containing 0%),
Nb:0.001% following (containing 0%),
V:0.001% following (containing 0%),
Zr:0.001% following (containing 0%),
B:0.0001% following (containing 0%),
Ta:0.0001% following (containing 0%),
Hf:0.0001% following (containing 0%), and satisfy following formula (2).
14[Al]/27+14[Ti]/47.9+14[Nb]/92.9+14[V]/50.9+14[Zr]/91.2+14[B]/10.8+14[Ta]/180.9+14[Hf]/178.5≤0.002% ... (2) formula
[[] represents the total content (quality %) of each element in steel in the formula (2)]
The steel for high-speed cold working of the 3rd embodiment of the present invention preferably also contains Cr:2% following (not containing 0%).
In steel for high-speed cold working of the present invention, except that mentioned component, it is also effective also to contain Cu:5% following (not containing 0%) as required.
With in the steel, except that mentioned component, it is also effective also to contain Ni:5% following (not containing 0%) and/or (not containing 0%) below the Co:5% as required in the cool processing of high speed of the present invention.
With in the steel, except that mentioned component, it is also effective also to contain Mo:2% following (not containing 0%) and/or (not containing 0%) below the W:2% as required in the cool processing of high speed of the present invention.
Use in the steel in the cool processing of high speed of the present invention, except that mentioned component, also contain as required the group who constitutes from following element select at least a kind also effective: (do not contain 0%) below the Ca:0.05%, rare earth element (following province is " REM " slightly): (do not contain 0%) below 0.05%, (do not contain 0%) below the Mg:0.02%, (do not contain 0%) below the Li:0.02%, (do not contain 0%) below the Pb:0.1% and (do not contain 0%) below the Bi:0.1%.
Steel for high-speed cold working of the present invention is recommended in processing temperature and is and is used for high speed cold processing under the condition below 200 ℃.In addition, being recommended in rate of straining is to be used for high speed cold processing under the above condition of 100/s.
Also have, rate of straining is to try to achieve according to the true strain that produces in the unit time.
As the manufacture method of steel for high-speed cold working of the present invention, to recommend to be as preferred a kind of mode, the steel that will have the mentioned component composition are heated to Ac
3Temperature more than point+30 ℃ is thereafter at Ac
3Temperature province more than point+30 ℃ is carried out hot-work, is cooled to method below 500 ℃ with the above speed of cooling of 0.5 ℃/s thereafter.
As the manufacture method of steel for high-speed cold working of the present invention, to recommend to be as preferred a kind of mode, the steel that will have the mentioned component composition are heated to Ac
3Temperature more than point+30 ℃ is cooled to method below 500 ℃ with the above speed of cooling of 0.5 ℃/s thereafter.
High-speed cold working part of the present invention, be that the part strength (H) after the preferred high speed cold processing and the maximum value (DR) of the resistance to deformation in the high speed cold processing satisfy following formula (3) by under the processing temperature below 200 ℃, with the rate of straining more than the 100/s above-mentioned steel for high-speed cold working is carried out the high-speed cold working part that high speed cold processing manufactures.
H≥(DR+1000)/6…(3)
Wherein, H: part strength, DR: resistance to deformation (MPa)
Steel for high-speed cold working of the present invention is (a) because contain solid solution N more than specified amount, so even the thermal treatment of the Q-tempering after the omission cold working also can be guaranteed the part strength of stipulating after cold working.Steel for high-speed cold working of the present invention in addition, (b) because of its purposes is restricted to high speed cold processing (preferred rate of straining is the above cold working of 100/s), and (c) the chemical ingredients amount is suitably changed, and therefore demonstrates good cold-workability.
Embodiment
Steel for high-speed cold working of the present invention, the maximum feature that has are to contain solid solution N more than specified amount.Feature in view of the above can be given steel part that high part strength guaranteed with good cold-workability.Yet, it is generally acknowledged, contain a large amount of solid solution N and can increase the resistance to deformation of steel and make metal pattern life-span deterioration, and the drawback that can cause that part cracks etc.The present invention is by under high speed and carry out cold working, thereby keeps good cold-workability.That is, steel of the present invention is feature to be limited to use under the such purposes of high speed cold processing.(a) by containing solid solution N more than amount, thereby the part strength after the cold working is improved, and (b) process the drawback that suppresses solid solution N by high speed cold, thereby keep good cold-workability, this technological thought did not have in the past.
In addition, carry out cold working under the high speed, can also help to improve the productivity and energy-conservationization of part.
The chemical ingredients of＜steel for high-speed cold working (basic mode of the present invention) 〉
The steel for high-speed cold working of basic mode of the present invention, in order to reach good cold-workability, one of feature is that the chemical ingredients amount is suitably changed, and therefore, below describes with regard to the chemical ingredients of steel and solid solution N amount.
(C：0.03～0.6％)
C is used to guarantee the intensity needed element of high speed cold processing with part.Therefore the C amount is decided to be more than 0.03%.More preferably more than 0.04%, more preferably more than 0.05%.On the other hand, if C measured at most by cutting property and cold-workability deterioration.Therefore the C amount on be defined as 0.6%.More preferably 0.5%, more preferably 0.4%.
(Si：0.005～0.6％)
Si is used as the element that reductor uses in system steel process.If the Si amount is few, then deoxidation deficiency produces gas thus in process of setting, and they will be had an effect as defective easily, therefore makes the energy of deformation deterioration.In order to bring into play its effect effectively, need to add more than 0.005%.More preferably be limited to 0.008% down, be limited to 0.01% under further preferred.Yet the surplus interpolation of Si causes the effect of deoxidation saturated, and the cold-workability deterioration.Therefore with the upper limit as 0.6%.Be limited to 0.5% on preferred.
(Mn：0.05～2％)
Mn is an effective elements as deoxidation/desulfurization element in the system process.If the Mn amount is few, then separate out with membranaceous at crystal grain boundary FeS, grain-boundary strength is significantly reduced, make the energy of deformation deterioration.In order to bring into play its effect effectively, need to add the Mn more than 0.05%.Be limited to 0.1% under preferred.Yet the surplus interpolation of Mn can make the cold-workability deterioration, so is limited to 2% on it.Be limited to 1.5% on preferred, be limited to 1% under further preferred.
(P:0.05% following (not containing 0%))
P is the element that contains as unavoidable impurities, but if P contains in ferrite, then at the ferrite grain boundary segregation, therefore makes the cold-workability deterioration.In addition, P makes the ferrite solution strengthening, and resistance to deformation is increased.Therefore,, preferably do one's utmost to reduce P from the viewpoint of cold-workability, but the increase that extreme reduction can cause making the steel cost.Therefore, consider cold-workability and process capability, and with the upper limit as 0.05%.More preferably below 0.03%.But making P amount is 0 industrial very difficult.
(S:0.05% following (not containing 0%))
S is the element that contains as unavoidable impurities, but it can form the MnS inclusion and make the energy of deformation deterioration.Therefore, preferably do one's utmost to reduce S, thus from the viewpoint of energy of deformation and with the upper limit as 0.05%.Preferred range is below 0.03%.On the other hand, S is an effective elements on improving by cutting property, and situation about actively containing is also arranged.If consider, then recommend to contain S, more preferably more than 0.006% preferably more than 0.002% by cutting property.
(N:0.04% following (not containing 0%))
At this, describe for the total N content in the steel.N is solid solution in steel, has the effect that the part strength after the cold working of making improves, and is important element in the present invention.Yet if the total N content surplus in the steel, solid solution N measures superfluous, when cold working crackle can take place.Crackle of steel billet when in addition, also the subsurface defect of generation steel is with continuous casting easily.Therefore, the viewpoint of the yield rate during from the stability of the energy of deformation that improves steel, material and continuous casting is defined as 0.04% on the total N content in the steel.Be limited to 0.03% on preferred.On the other hand, in basic mode of the present invention,, in order to satisfy the lower limit amount of solid solution N described later, and preferably contain more than 0.007% though the lower limit of total N content does not have special stipulation, more preferably more than 0.008%, further preferred more than 0.009%.
(more than the solid solution N:0.006%)
Solid solution N such as above-mentioned has the effect that the part strength after the high speed cold of making is processed improves.In order fully to guarantee the last ascending effect of the part strength after high speed cold is processed, will be defined as 0.006% under it.Preferred lower limit is 0.007%, is limited to 0.008% under further preferred.On the other hand, if solid solution N amount surplus, then energy of deformation deterioration.Therefore, solid solution N amount is preferably below 0.035%, more preferably below 0.030%, more preferably below 0.025%.Also have, solid solution N amount surely not surpasses the total N content in the steel.Here, the value of " solid solution N amount " among the present invention can be according to JIS G 1228, calculates solid solution N amount in the tapping by deducting whole N compounds in the total N content from steel.
(a) total N content in the steel adopts the rare gas element method of melting-thermal conductivity method.From for the former material of examination steel cutting sample down, sample is put into crucible, in inert gas flow, melted and extracted N, be transported to the variation that the thermal conductivity instrument is measured thermal conductivity.
(b) the blue spectrophotometry of whole N compound portion's employing ammonia fractionation by distillation indophenols (indophenol) in the steel.From cutting sample down for the former material of examination steel, at 10%AA is that electrolytic solution (is the electrolytic solution that can not make the surperficial non-water-soluble matchmaker who generates non-dynamic epithelium of steel be, be exactly 10% methyl ethyl diketone (acetylacetone) specifically, 10% tetramethylammonium chloride (tetramethylammonium chloride), surplus: methyl alcohol), carry out deciding current electroanalysis.Making about 0.5g sample dissolution, is that the strainer of polycarbonate (polycarbonate) system of 0.1 μ m filters to dissolved residue (N compound) not with hole dimension.In sulfuric acid, vitriolate of tartar and pure Cu sheet, incite somebody to action not dissolved residue thermal degradation, make it to combine with filtrate.After making this solution be alkalescence with sodium hydroxide, carry out wet distillation, the ammonia that distills out is absorbed in the dilute sulphuric acid.Add phenol (phenol), clorox (sodium hypochlorite) and the sour sodium cyanide dihydrate of iron nitrosyl (III) (Sodiumpentacyanonitrosylferrate (III) dihydrate) and blue complex is generated, use its absorbancy of photometric determination.
Total N content from the steel of trying to achieve according to aforesaid method deducts whole N compound amounts, thereby calculates the solid solution N amount in the tapping.
The basal component of the steel of basic mode of the present invention is formed as mentioned above, and surplus comes down to iron.But, also allow to be included in the steel certainly because of the unavoidable impurities that the situation of raw material, goods and materials, manufacturing maintenance etc. is sneaked into.The steel of basic mode of the present invention also can contain following arbitrary element as required in addition.
(Al:0.1% following (not containing 0%))
Al is an effective elements as the deoxidant element in the system steel operation basically, also is effective elements on the anti-crackle of steel in addition.Recommend to contain Al as required and be preferably more than 0.001%, more preferably more than 0.005%.But the avidity of Al and N is strong, can form Al N and solid solution N amount is reduced, therefore in basic mode of the present invention, make it to contain sometimes on be defined as 0.1%.The Al amount is preferably below 0.05%, more preferably below 0.03%.
(below Zr:0.2%, (not containing 0%), (do not contain 0%) below the Ti:0.1%, (do not contain 0%) below the Nb:0.1%, (do not contain 0%) below the V:0.5%, (do not contain 0%) below the Ta:0.1% and (do not contain 0%) below the Hf:0.1% at least a kind that selects the group who is constituted)
Zr, Ti, Nb, V, Ta, Hf and N can form the N compound and make grain refining, are effective elements substantially on the toughness of resulting part after being used to improve cold working.Therefore in basic mode of the present invention, as required, recommend to contain Zr and be preferably more than 0.002%, more preferably more than 0.004%, containing Ti is preferably more than 0.001%, more preferably more than 0.002%, contain Nb and be preferably more than 0.001%, more preferably more than 0.002%, containing Ta is preferably more than 0.003%, more preferably more than 0.006%, contain Hf and be preferably more than 0.002%, more preferably more than 0.004%.
On the other hand, the avidity of these elements and N is strong, can form the N compound and solid solution N amount is reduced, and therefore in basic mode of the present invention, determines the upper limit as follows.The Zr amount is below 0.2%, is preferably below 0.1%, more preferably below 0.05%, more preferably below 0.03%, the Ti amount is below 0.1%, is preferably below 0.05%, more preferably below 0.03%, the Nb amount is below 0.1%, be preferably below 0.06%, more preferably below 0.04%, the V amount is below 0.5%, be preferably below 0.2%, more preferably below 0.1%, more preferably below 0.05%, be preferably below 0.03% especially, the Ta amount is below 0.1%, be preferably below 0.05%, more preferably below 0.03%, the Hf amount is below 0.1%, be preferably below 0.05%, more preferably below 0.03%.
(B:0.0015% following (not containing 0%))
B is the element that the energy of deformation of steel is improved by the intensity that improves crystal grain boundary.Therefore in basic mode of the present invention, recommend to contain B as required and be preferably more than 0.0001%, more preferably more than 0.0002%.But the avidity of B and N is strong, can form BN and solid solution N amount is reduced.In addition, if the BN surplus, then cold-workability reduces.Therefore contain sometimes, the B amount of basic mode of the present invention is below 0.0015%, is preferably below 0.001%, more preferably below 0.0008%.
(Cr:2% following (not containing 0%))
Cr is the same with B, and the energy of deformation of steel is improved.Therefore recommend to contain Cr as required and be preferably more than 0.1%, more preferably more than 0.2%.But, the then resistance to deformation increase of surplus if Cr also becomes, cold-workability reduces.Therefore contain sometimes, the Cr amount is below 2%, is preferably below 1.5%, more preferably below 1%.
(Cu:5% following (not containing 0%)
Because having the steel of making, Cu produces strain aging and the hardened effect, so can improve the part strength after the processing.Therefore recommend preferably to contain more than 0.1%, more preferably more than 0.5%.Yet, also be saturated even add its effect superfluously, can not expect and the content corresponding effects, on economy unfavorable, also cause the deterioration of cold-workability, produce the problems such as surface texture deterioration of part.Therefore, Cu on be limited to 0.5%.Be preferably below 4%, more preferably below 3%, more preferably below 2%.
(Ni:5% following (not containing 0%) and/or Co:5% following (not containing 0%))
Ni is effective aspect the energy of deformation that improves ferrite pearlific steel.Preventing of the surface imperfection that takes place at steel surface during in addition, for interpolation Cu is also effective.Recommendation preferably contains promising more than 0.1%, more preferably more than 0.5%.Therefore when adding Cu, the Ni of preferred interpolation and Cu are with amount or more than 7 one-tenth of Cu amount.Yet, also be saturated even add to surpass 5% effect, can not expect and the content corresponding effects, on economy unfavorable, cold-workability is deterioration on the contrary.Therefore the Ni amount on be limited to 5%.The Ni amount is preferably below 4%, more preferably below 3%, more preferably below 2%.
Co is the same with Ni, and is effective aspect the energy of deformation that improves ferrite pearlific steel.Recommend preferably to contain more than 0.1%, more preferably more than 0.5%.Yet if surpass 5%, in casting, rolling etc. manufacturing process, grain-boundary strength is reduced, be easy to generate crackle, thus the Co amount on be limited to 5%.The Co amount is preferably below 4%, more preferably below 3%, more preferably below 2%.
(Mo:2% following (not containing 0%) and/or W:2% following (not containing 0%))
Mo has the effect that hardness after the processing of making and energy of deformation increase.Therefore, recommend preferably to contain more than 0.04%, more preferably more than 0.08%, more preferably more than 0.1%.Yet, surpass 2% interpolation and make the cold-workability deterioration.Therefore, Mo amount on be limited to 2%.The Mo amount is preferably below 1.5%, more preferably below 1%.
W is the same with Mo, has the effect that hardness after the processing of making and energy of deformation increase.Therefore, recommend to make it preferably to contain more than 0.04%, more preferably more than 0.08%, more preferably more than 0.1%.Yet, surpass 2% interpolation and make the cold-workability deterioration.Therefore, W amount on be limited to 2%.The W amount is preferably below 1.5%, more preferably below 1%, more preferably below 0.5%.
(below Ca:0.05%, below the REM:0.05%, below the Mg:0.02%, below the Li:0.02%, below the Pb:0.1% and select the group who is constituted below the Bi:0.1% at least a kind)
Ca, REM, Mg, Li, Pb and Bi are the elements that helps cutting property of the quilt raising of steel.Especially can to make Al be that the oxide compound eutectic is revealed to Li, innoxious, and machinability is improved.Ca, REM, Mg and Li make the sulfide-based inclusion balling of MnS etc. in addition, also have the toughness that improves steel and the effect of energy of deformation.Therefore recommend to contain with following amount: Ca is preferably more than 0.005%, more preferably more than 0.01%, REM is preferably more than 0.005%, more preferably more than 0.01%, Mg is preferably more than 0.002%, more preferably more than 0.005%, more preferably more than 0.008%, Li is preferably more than 0.001%, more preferably more than 0.002%, more preferably more than 0.005%, Pb is preferably more than 0.005%, more preferably more than 0.01%, more preferably more than 0.02%, and Bi is preferably more than 0.005%, more preferably more than 0.01%, more preferably more than 0.02%.
But even these amount of element surpluses, its effect also is saturated.In addition if Pb amount is superfluous, then produce the problem that roll marks etc. is made.Therefore stipulate to contain upper limit amount sometimes in the following manner.The Ca amount is preferably below 0.04%, more preferably below 0.03%, more preferably below 0.02%, the REM amount is preferably below 0.04%, more preferably below 0.03%, more preferably below 0.02%, be preferably below 0.01% especially, the Mg amount is preferably below 0.018%, more preferably below 0.015%, more preferably below 0.01%, the Li amount is preferably below 0.018%, more preferably below 0.015%, more preferably below 0.01%, the Pb amount is preferably below 0.09%, more preferably below 0.08%, more preferably below 0.06%, and the Bi amount is preferably below 0.09%, more preferably below 0.08%.
(manufacture method of steel for high-speed cold working)
Next, the manufacture method for steel for high-speed cold working of the present invention describes.Steel of the present invention is to be feature more than 0.006% to contain solid solution N amount.In order to ensure this solid solution N amount, effectively the total N content in the steel is increased by (i), reduce with the high element of the avidity of N and (ii) steel is heated to more than the specified temperature, more than the speed of cooling of regulation, cool off, improve solid solution N thus and measure.
(i) make the total N content in the steel increase the method for the element that the avidity of reduction and N is high
When steel contained the strong element of Al etc. and N avidity, the result of formation N compounds such as nitrogen and Al was that solid solution N amount reduces.But,,, still can guarantee sufficient solid solution N amount even then Al etc. forms the N compounds with whole N if the total N content in the steel is than more.More particularly, guarantee total N content like this, just can guarantee the solid solution N amount more than 0.006% by satisfying following formula (1).
[N]-(14[Al]/27+14[Ti]/47.9+14[Nb]/92.9+14[V]/50.9+14[Zr]/91.2+14[B]/10.8+14[Ta]/180.9+14[Hf]/178.5) 〉=0.006 ... (1) formula
[[] represents the total content (quality %) of each element in steel in the formula (1)]
(ii), more than the speed of cooling of regulation, cool off, thereby improve the method that solid solution N measures by steel being heated to more than the temperature of regulation
In addition, if the chemical constitution in the steel does not satisfy (1) formula, the N compound of Al etc. is formed in a large number, in the time of can not guaranteeing that sufficient solid solution N measures, steel heated remain on the N compound dissolution that forms through hot rolling etc. in the temperature of sosoloid, chilling suppresses the solution heat treatment of separating out of N compound afterwards, and solid solution N amount is increased.Specifically, exactly by steel is heated to Ac
3After the temperature more than point+30 ℃, the speed of cooling above with 0.5 ℃/s is cooled to below 500 ℃, thereby the solid solution N amount in the steel is increased.
In order to increase solid solution N amount, Heating temperature is Ac
3More than point+30 ℃, be preferably Ac
3More than point+40 ℃, Ac more preferably
3More than point+50 ℃.The heating hold-time was preferably more than 10 minutes, more preferably more than 30 minutes.But from the viewpoint of manufacturing cost, Heating temperature is Ac
3Below point+500 ℃, Ac more preferably
3Below point+450 ℃, Ac more preferably
3Below point+400 ℃, be preferably Ac especially
3Below point+300 ℃.In addition, the heating hold-time is preferably 2 advances below 30 minutes for a short time, and more preferably 1 hour below 30 minutes.
In this heating keeps, also can carry out the hot-work of wire drawing, rolling or extruding etc. aptly.After heating keeps, preferably above with 0.5 ℃/s, more preferably 1 ℃/s, further the above speed of cooling of preferred 5 ℃/s is cooled to below 500 ℃ of solid solution N stable existence, preferably be cooled to below 450 ℃, can suppress separating out of N compound thus, guarantee sufficient solid solution N amount.
(manufacture method of high-speed cold working part)
One of feature of the present invention is that the steel that contains above-mentioned chemical constitution and solid solution N amount is specialized in high speed cold processing.Though steel of the present invention contains solid solution N more in large quantities, but in order to keep good cold-workability, recommend preferably with more than the 100/s, more preferably with more than the 120/s, further preferably with more than the 140/s, more than the preferred especially 150/s, most preferably the rate of straining more than the 200/s carries out cold working.On the other hand, if rate of straining is too fast, the temperature that heat insulating ability then takes place rises, generation crackle, so rate of straining easily is preferably below the 500/s, more preferably below the 450/s, more preferably below the 400/s, be preferably especially below the 300/s, most preferably be below the 280/s, especially be preferably below the 260/s.
In addition,,, more preferably be set at 180 ℃, further be preferably set to 160 ℃ so recommend the higher limit of processing temperature to be preferably set to 200 ℃ because the temperature in the processing also can influence cold-workability.If processing temperature is too high, in the distortion dynamic strain aging takes place then, resistance to deformation is risen, metal pattern life-span deterioration.On the other hand, though cold working is at room temperature implemented usually, if be lower than 0 ℃, then under the influence of temperature dependency, resistance to deformation uprises on the contrary, so the preferred lower limit of processing temperature is 0 ℃.Also have, processing temperature is the atmosphere temperature in the processing.
The steel of Zhi Zaoing (for example wire rod and bar steel) are processed by high speed cold under above-mentioned condition afterwards as above, become part and other mechanical component of bolt/nut etc.Here in the said cold process, comprise cold forging, cold pressing, cold working such as cold rolling, cold drawing, cold extrusion.In addition, if part be processed with needs, also can carry out position silk, rolling etc. processing.
Process the part of making by high speed cold, the balance of the resistance to deformation in preferred features intensity and the high speed cold processing is suitable, with the processing temperature below 200 ℃, rate of straining more than the 100/s steel for high-speed cold working is carried out high speed cold and add man-hour, the part strength (H) after the preferred high speed cold processing and the maximum value (DR) of the resistance to deformation in the high speed cold processing satisfy following formula (3).
H 〉=(DR+1000)/6 ... (3) formula
Wherein, H: part strength (Hv), DR: resistance to deformation (MPa).
(the embodiments of the present invention)
The composition of the basal component of the steel of basic mode of the present invention and selection component (arbitrary element) as mentioned above.But according to purposes and desired performance, basic mode of the present invention can be categorized as following 3 kinds of embodiments.
(first embodiment of the present invention)
The steel for high-speed cold working of first embodiment of the present invention, contain C:0.03%～0.15%, Si:0.005～0.6%, Mn:0.05～2%, P:0.05% following (not containing 0%), S:0.05% following (not containing 0%) and N:0.04% following (not containing 0%), surplus is made of iron and unavoidable impurities, and the solid solution nitrogen amount in the steel is more than 0.006%.
(C：0.03％～0.15％)
In first embodiment of the present invention,, will be defined as 0.15% on the C amount in order to realize good cutting property of quilt and cold-workability.Be limited to 0.12% on preferred.In order to ensure the intensity of steel, the following of C is limited to 0.03%, is preferably 0.04%.
Explanation in first embodiment of the present invention beyond the C amount (promptly, the explanation of the balance (following formula (3)) of the resistance to deformation in the manufacture method of other basal component and selection component (arbitrary element), steel, the manufacture method of part, part strength and the high speed cold processing etc.), with set forth in the basic mode of the present invention identical.
(second embodiment of the present invention)
The steel for high-speed cold working of second embodiment of the present invention, contain C:0.15%～0.6% respectively but do not comprise 0.15%, Si:0.005～0.6%, Mn:0.05～2%, P:0.05% following (not containing 0%), S:0.05% following (not containing 0%) and below the N:0.04% (not containing 0%), surplus is made of iron and unavoidable impurities, is more than 0.006% as the content of the N of solid solution condition.
(C:0.15%～0.6% but do not comprise 0.15%)
In second embodiment of the present invention, the C amount is decided to be above 0.15% in order to realize higher part strength.More preferably more than 0.16%, more preferably more than 0.17%.On the other hand, if C measured at most by cutting property and cold-workability deterioration.Therefore the C amount on be limited to 0.6%, be preferably 0.5%, more preferably 0.4%.
Explanation in second embodiment of the present invention beyond the C amount (promptly, the explanation of the balance (following formula (3)) of the resistance to deformation in the manufacture method of other basal component and selection component (arbitrary element), steel, the manufacture method of part, part strength and the high speed cold processing etc.), with set forth in the basic mode of the present invention identical.
(the 3rd embodiment of the present invention)
In the 3rd embodiment of the present invention, recorded and narrated the amount that can reduce the element (Al, Ti, Nb, V, Zr, B, Ta, Hf) of solid solution N about reduction.In view of the above, can guarantee sufficient solid solution N amount, promptly can keep good cold-workability, can reach higher part strength again.
It is the steel for high-speed cold working of the 3rd embodiment of the present invention, contain C:0.03%～0.6%, Si:0.005～0.6%, Mn:0.05～2%, P:0.05% following (not containing 0%), S:0.05% following (not containing 0%), N:0.008～0.04%, surplus is made of iron and unavoidable impurities, in this impurity, satisfy Al:0.001% following (not containing 0%), Ti:0.002% following (not containing 0%), Nb:0.001% following (not containing 0%), V:0.001% following (not containing 0%), Zr:0.001% following (not containing 0%), B:0.0001% following (not containing 0%), Ta:0.0001% following (not containing 0%), Hf:0.0001% following (not containing 0%), and satisfy following formula (2).
14[Al]/27+14[Ti]/47.9+14[Nb]/92.9+14[V]/50.9+14[Zr]/91.2+14[B]/10.8+14[Ta]/180.9+14[Hf]/178.5≤0.002% ... (2) formula
[[] represents the total content (quality %) of each element in steel in the formula (2)]
(N：0.008～0.04％)
The lower limit of the total N content of the 3rd embodiment of the present invention is in order to ensure solid solution N amount and as 0.008%.Preferred lower limit is 0.009%.On the other hand, the viewpoint that the yield rate during from the stability of the energy of deformation of steel, material and continuous casting improves is limited to 0.04% on the total N content, be preferably 0.03%.
As unavoidable impurities, the situation that comprises Al, Ti, Nb, V, Zr, B, Ta, Hf is arranged.These Al etc. combine with solid solution N easily, have the effect of the solid solution N amount that reduces in the steel.Therefore in the 3rd embodiment of the present invention, the content regulation when containing these elements is as follows.
(Al:0.001% following (not containing 0%), Ti:0.002% following (not containing 0%), Nb:0.001% following (not containing 0%), V:0.001% following (not containing 0%), Zr:0.001% following (not containing 0%), B:0.0001% following (not containing 0%), Ta:0.0001% following (not containing 0%), Hf:0.0001% following (not containing 0%)).
Al, Ti, Nb, V, Zr, B, Ta, Hf combine with solid solution N, and solid solution N amount is reduced, and form nitride (AlN, TiN, NbN, VN, ZrN, BN, TaN, HfN).These nitride play a role on ending in separate out intensity and the thick chemoprevention of crystal grain of steel, and resistance to deformation is increased.In order to ensure sufficient solid solution N amount, and reach good resistance to deformation, the amount of Al etc. is low more super good.
Therefore the Al amount is below 0.001% in the 3rd embodiment of the present invention, be preferably below 0.0005%, the Ti amount is below 0.002%, be preferably below 0.001%, the Nb amount is below 0.001%, be preferably below 0.0005%, the V amount is below 0.001%, is preferably below 0.0005%, the Zr amount is below 0.001%, be preferably below 0.0005%, the B amount is below 0.0001%, is preferably below 0.00005%, the Ta amount is below 0.0001%, be preferably below 0.00005%, the Hf amount is below 0.0001%, to be preferably below 0.00005%.The most preferred content of Al, Ti, Nb, V, Zr, B, Ta and Hf is respectively 0%.
Though the content of Al, Ti, Nb, V, Zr, B, Ta, Hf need in order to ensure sufficient solid solution N amount in the steel, also need to satisfy the relation of following formula (2) respectively below afore mentioned rules.
14[Al]/27+14[Ti]/47.9+14[Nb]/92.9+14[V]/50.9+14[Zr]/91.2+14[B]/10.8+14[Ta]/1 80.9+14[Hf]/178.5≤0.002% ... (2) formula
For example (14[Al]/27) this be the item that is illustrated in the nitrogen amount in the steel that is present under the form of AlN, (2) left side of formula is all, the total of the nitrogen amount of each bonding state of expression and Al, Ti, Nb, V, Zr, B, Ta, Hf (total of the N compound amount in the steel).Therefore, in order to ensure solid solution N amount, therefore the preferred little side of N compound amount is below 0.002%.More preferably below 0.0018%, more preferably below 0.0016%.
Explanation beyond N, Al in the 3rd embodiment of the present invention, Ti, Nb, V, Zr, B, Ta and the Hf amount (promptly, the explanation of the balance (following formula (3)) of the resistance to deformation in the manufacture method of other basal component and selection component (arbitrary element), steel, the manufacture method of part, part strength and the high speed cold processing etc.), with set forth in the basic mode of the present invention identical.Also have, in the 3rd embodiment of the present invention, also can make steel for high-speed cold working,, then need not rely on manufacturing process basically and just can guarantee that the solid solution N in the steel measures if satisfy formula (2) by above-mentioned manufacture method.
[embodiment]
Below enumerate embodiment and illustrate in greater detail the present invention, but the present invention is not limited by following examples, can certainly be before meeting be suitably changed enforcement in the scope of aim described later, these all are included in the technical scope of the present invention.
＜embodiment 1 (about the example of the present invention and the comparative example of first embodiment of the invention) 〉
At first, utilize the converter melting to have the steel that the described chemical ingredients of table 1～table 3 is formed, after making it to become steel billet by continuous casting, be rolled into the wire rod of 12mm.
The thermal treatment of condition shown in carry out table 4 for the wire rod that obtains.After the heat treated of the condition shown in carry out table 4, hope is set more than 10 minutes, the preferred hold-time more than 30 minutes.Secondly, from having implemented the central part of above-mentioned heat treated wire rod, cutting is the test film of 4mm * long 6mm down.Also have, show also in table 1～table 3 whether each test film satisfies following formula (1), is designated as " zero " when satisfying formula (1), be designated as when not satisfying (1) formula " * ".In addition, " solid solution N " expression solid solution N amount in the table, " N " represents total nitrogen.
[table 1]
| Material No. | The steel mark | Chemical constitution (quality %) | Ac 3The point (℃) | Solid solution N quality % | (1) whether formula is set up | Thermal treatment | ||||||||||||||
| C | Si | Mn | P | S | N | Al | Ti | Nb | V | Zr | B | Ya | Hf | Other | ||||||
| I-1 | I-1A | 0.02 | 0.07 | 0.15 | 0.015 | 0.015 | 0.0095 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 891 | 0.0081 | ○ | I-a |
| I-2 | I-1B | 0.05 | 0.17 | 0.44 | 0.009 | 0.012 | 0.0167 | 0.012 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 871 | 0.0096 | ○ | I-h |
| I-3 | I-1C | 0.06 | 0.15 | 0.32 | 0.023 | 0.028 | 0.0103 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 874 | 0.0089 | ○ | I-d |
| I-4 | I-1D | 0.11 | 0.12 | 0.23 | 0.018 | 0.021 | 0.0145 | 0.008 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 857 | 0.0095 | ○ | I-i |
| I-5 | I-1E | 0.13 | 0.06 | 0.14 | 0.008 | 0.008 | 0.0155 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 842 | 0.0141 | ○ | I-j |
| I-6 | I-1F | 0.17 | 0.06 | 0.14 | 0.008 | 0.008 | 0.0155 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 831 | 0.0141 | ○ | I-b |
| I-7 | I-1G | 0.08 | 0.002 | 0.27 | 0.013 | 0.012 | 0.0189 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 855 | 0.0175 | ○ | I-j |
| I-8 | I-1H | 0.1 | 0.18 | 0.35 | 0.006 | 0.004 | 0.0169 | 0.013 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 853 | 0.0093 | ○ | I-j |
| I-9 | I-1I | 0.08 | 0.23 | 0.1 | 0.005 | 0.032 | 0.0123 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 864 | 0.0109 | ○ | I-h |
| I-10 | I-1J | 0.12 | 0.38 | 0.19 | 0.007 | 0.015 | 0.0175 | 0.009 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 860 | 0.0120 | ○ | I-d |
| I-11 | I-1K | 0.09 | 0.4 | 0.13 | 0.015 | 0.008 | 0.0093 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 874 | 0.0079 | ○ | I-i |
| I-12 | I-1L | 0.11 | 0.57 | 0.29 | 0.009 | 0.034 | 0.0217 | 0.005 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 868 | 0.0183 | ○ | I-f |
| I-13 | I-1M | 0.05 | 0.58 | 0.41 | 0.018 | 0.013 | 0.0193 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 891 | 0.0179 | ○ | I-h |
| I-14 | I-1N | 0.08 | 0.62 | 0.21 | 0.009 | 0.028 | 0.0098 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 881 | 0.0084 | ○ | I-b |
| I-15 | I-1O | 0.06 | 0.39 | 0.03 | 0.045 | 0.041 | 0.0241 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 909 | 0.0227 | ○ | I-g |
| I-16 | I-1P | 0.09 | 0.17 | 0.24 | 0.019 | 0.034 | 0.0151 | 0.006 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 866 | 0.0111 | ○ | I-g |
| I-17 | I-1Q | 0.09 | 0.34 | 0.22 | 0.043 | 0.019 | 0.0087 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 889 | 0.0073 | ○ | I-d |
| I-18 | I-1R | 0.13 | 0.54 | 0.45 | 0.032 | 0.002 | 0.0315 | 0.015 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 876 | 0.0229 | ○ | I-e |
| I-19 | I-1S | 0.06 | 0.56 | 0.48 | 0.008 | 0.009 | 0.0316 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 877 | 0.0302 | ○ | I-c |
| I-20 | I-1T | 0.08 | 0.43 | 1.03 | 0.005 | 0.043 | 0.0252 | 0.023 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 854 | 0.0124 | ○ | I-j |
| I-21 | I-1U | 0.06 | 0.17 | 1.15 | 0.034 | 0.015 | 0.0197 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 858 | 0.0183 | ○ | I-f |
| I-22 | I-1V | 0.15 | 0.16 | 1.89 | 0.004 | 0.032 | 0.0285 | 0.015 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 791 | 0.0199 | ○ | I-b |
| I-23 | I-1W | 0.11 | 0.08 | 1.95 | 0.024 | 0.011 | 0.0144 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 805 | 0.0130 | ○ | I-i |
| I-24 | I-1X | 0.14 | 0.15 | 2.08 | 0.028 | 0.019 | 0.0198 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 799 | 0.0184 | ○ | I-h |
| I-25 | I-1Y | 0.13 | 0.35 | 0.27 | 0.06 | 0.004 | 0.0175 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 887 | 0.0161 | ○ | I-d |
| I-26 | I-1Z | 0.12 | 0.17 | 0.31 | 0.09 | 0.016 | 0.0307 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 902 | 0.0293 | ○ | I-g |
| I-27 | I-2A | 0.08 | 0.49 | 0.79 | 0.033 | 0.07 | 0.0108 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 875 | 0.0094 | ○ | I-a |
| I-28 | I-2B | 0.09 | 0.35 | 0.54 | 0.009 | 0.09 | 0.0108 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 856 | 0.0094 | ○ | I-f |
| I-29 | I-2C | 0.12 | 0.08 | 0.34 | 0.012 | 0.013 | 0.0061 | 0.008 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 845 | 0.0011 | × | I-j |
| I-30 | I-2D | 0.14 | 0.25 | 0.61 | 0.013 | 0.008 | 0.0075 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 837 | 0.0061 | ○ | I-e |
| I-31 | I-2E | 0.08 | 0.19 | 0.45 | 0.005 | 0.005 | 0.0195 | 0.011 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 856 | 0.0129 | ○ | I-g |
| I-32 | I-2F | 0.05 | 0.04 | 0.08 | 0.021 | 0.011 | 0.0199 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 880 | 0.0185 | ○ | I-h |
| I-33 | I-2G | 0.09 | 0.17 | 0.16 | 0.017 | 0.012 | 0.0256 | 0.005 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 866 | 0.0222 | ○ | I-c |
| I-34 | I-2H | 0.14 | 0.45 | 0.34 | 0.025 | 0.004 | 0.0218 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 862 | 0.0204 | ○ | I-d |
| I-35 | I-2I | 0.08 | 0.31 | 0.23 | 0.021 | 0.019 | 0.0335 | 0.014 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 880 | 0.0254 | ○ | I-f |
[table 2]
| Material No. | The steel mark | Chemical constitution (quality %) | Ac 3The point (℃) | Solid solution N quality % | (1) whether formula is set up | Thermal treatment | ||||||||||||||
| C | Si | Mn | P | S | N | Al | Ti | Nb | V | Zr | B | Ta | Hf | Other | ||||||
| I-36 | I-2J | 0.04 | 0.29 | 0.09 | 0.01 | 0.022 | 0.0376 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 887 | 0.0362 | ○ | I-b |
| I-37 | I-2K | 0.07 | 0.25 | 1.86 | 0.008 | 0.025 | 0.0443 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 818 | 0.0429 | ○ | I-i |
| I-38 | I-2L | 0.09 | 0.5 | 0.94 | 0.004 | 0.009 | 0.0231 | 0.001 | 0.04 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 862 | 0.0103 | ○ | I-g |
| I-39 | I-2M | 0.12 | 0.11 | 0.75 | 0.011 | 0.032 | 0.0285 | 0.006 | 0.001 | 0.03 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 833 | 0.0202 | ○ | I-i |
| I-40 | I-2N | 0.13 | 0.25 | 0.34 | 0.016 | 0.006 | 0.0229 | 0.001 | 0.001 | 0.06 | 0.02 | 0.000 | 0.0001 | 0 | 0 | - | 852 | 0.0074 | ○ | I-d |
| I-41 | I-2O | 0.09 | 0.38 | 0.41 | 0.023 | 0.015 | 0.0223 | 0.007 | 0.001 | 0.001 | 0.001 | 0.050 | 0.0001 | 0 | 0 | - | 873 | 0.0101 | ○ | I-c |
| I-42 | I-2P | 0.14 | 0.05 | 0.54 | 0.039 | 0.027 | 0.0099 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0006 | 0 | 0 | - | 848 | 0.0079 | ○ | I-e |
| I-43 | I-2Q | 0.05 | 0.17 | 0.13 | 0.019 | 0.005 | 0.0398 | 0.023 | 0.03 | 0.001 | 0.04 | 0.000 | 0.0001 | 0 | 0 | - | 907 | 0.0078 | ○ | I-h |
| I-44 | I-2R | 0.07 | 0.35 | 0.88 | 0.021 | 0.002 | 0.0308 | 0.018 | 0.001 | 0.04 | 0.001 | 0.005 | 0.0001 | 0 | 0 | - | 868 | 0.0140 | ○ | I-f |
| I-45 | I-2S | 0.09 | 0.16 | 1.23 | 0.025 | 0.015 | 0.0185 | 0.001 | 0.001 | 0.001 | 0.03 | 0.004 | 0.0001 | 0 | 0 | - | 841 | 0.0085 | ○ | I-j |
| I-46 | I-2T | 0.11 | 0.33 | 0.14 | 0.027 | 0.013 | 0.0212 | 0.009 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0.02 | 0 | - | 876 | 0.0137 | ○ | I-a |
| I-47 | I-2U | 0.1 | 0.28 | 0.31 | 0.038 | 0.03 | 0.0301 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0.05 | - | 876 | 0.0248 | ○ | I-c |
| I-48 | I-2V | 0.09 | 0.16 | 0.44 | 0.041 | 0.019 | 0.0232 | 0.018 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0013 | 0 | 0.03 | - | 879 | 0.0091 | ○ | I-g |
| I-49 | I-2W | 0.05 | 0.13 | 0.3 | 0.016 | 0.044 | 0.0388 | 0.001 | 0.05 | 0.001 | 0.05 | 0.000 | 0.0001 | 0 | 0 | - | 898 | 0.0096 | ○ | I-i |
| I-50 | I-2X | 0.09 | 0.32 | 0.22 | 0.017 | 0.015 | 0.0342 | 0.034 | 0.001 | 0.001 | 0.001 | 0.020 | 0.0001 | 0.01 | 0 | - | 883 | 0.0116 | ○ | I-e |
| I-51 | I-2Y | 0.11 | 0.38 | 1.53 | 0.019 | 0.009 | 0.0199 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0.03 | - | 828 | 0.0162 | ○ | I-h |
| I-52 | I-2Z | 0.13 | 0.56 | 0.09 | 0.022 | 0.018 | 0.0371 | 0.028 | 0.01 | 0.04 | 0.001 | 0.000 | 0.0001 | 0 | 0 | - | 890 | 0.0132 | ○ | I-b |
| I-53 | I-3A | 0.08 | 0.44 | 0.32 | 0.008 | 0.009 | 0.0233 | 0.001 | 0.01 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | Co：4.5 | 873 | 0.0193 | ○ | I-d |
| I-54 | I-3B | 0.12 | 0.22 | 0.43 | 0.005 | 0.045 | 0.0243 | 0.008 | 0.01 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | Mo：0.04，Pb：0.08 | 847 | 0.0167 | ○ | I-c |
| I-55 | I-3C | 0.09 | 0.12 | 0.12 | 0.012 | 0.019 | 0.0198 | 0.005 | 0.01 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | Mo：1.3 | 865 | 0.0137 | ○ | I-f |
| I-56 | I-3D | 0.04 | 0.08 | 0.65 | 0.015 | 0.003 | 0.0188 | 0.003 | 0.03 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | W：1.8 | 877 | 0.0079 | ○ | I-a |
| I-57 | I-3E | 0.08 | 0.09 | 0.99 | 0.009 | 0.023 | 0.0276 | 0.012 | 0.01 | 0.001 | 0.001 | 0.000 | 0.0008 | 0 | 0 | W：0.05，Ca：0.016 | 842 | 0.0170 | ○ | I-e |
| I-58 | I-3F | 0.04 | 0.13 | 0.15 | 0.003 | 0.019 | 0.0324 | 0.010 | 0.01 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | Ca：0.008 | 881 | 0.0237 | ○ | I-j |
| I-59 | I-3G | 0.06 | 0.12 | 1.22 | 0.034 | 0.039 | 0.0355 | 0.001 | 0.01 | 0.001 | 0.001 | 0.005 | 0.0001 | 0.01 | 0 | Ca：0.02，REM：0.009 | 857 | 0.0301 | ○ | I-g |
| I-60 | I-3H | 0.1 | 0.08 | 0.56 | 0.028 | 0.011 | 0.0180 | 0.001 | 0.01 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | REM：0.042 | 857 | 0.0140 | ○ | I-j |
| I-61 | I-3I | 0.11 | 0.09 | 0.43 | 0.018 | 0.031 | 0.0233 | 0.001 | 0.01 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | Mg：0.01，Cr：1.3 | 851 | 0.0193 | ○ | I-c |
| I-62 | I-3J | 0.05 | 0.21 | 0.39 | 0.011 | 0.008 | 0.0154 | 0.004 | 0.01 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | Li：0.005 | 876 | 0.0098 | ○ | I-b |
| I-63 | I-3K | 0.09 | 0.39 | 0.28 | 0.032 | 0.015 | 0.0198 | 0.001 | 0.01 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | Mg：0.013，Ca：0.003 | 885 | 0.0155 | ○ | I-i |
| I-64 | I-3L | 0.14 | 0.43 | 0.11 | 0.008 | 0.026 | 0.0221 | 0.009 | 0.01 | 0.001 | 0.01 | 0.000 | 0.0001 | 0 | 0 | Co：2.5，Mo：0.3 | 864 | 0.0115 | ○ | I-f |
| I-65 | I-3M | 0.11 | 0.19 | 0.17 | 0.01 | 0.007 | 0.0308 | 0.001 | 0.01 | 0.02 | 0.001 | 0.000 | 0.0001 | 0 | 0 | Cu：0.4 | 857 | 0.0239 | ○ | I-e |
| I-66 | I-3N | 0.08 | 0.27 | 0.35 | 0.008 | 0.012 | 0.0203 | 0.005 | 0.01 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | Cu：3.2.Cr：0.8 | 866 | 0.0142 | ○ | I-e |
| I-67 | I-3O | 0.12 | 0.31 | 0.28 | 0.035 | 0.019 | 0.0198 | 0.002 | 0.01 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0 | Cu：1.3，Ni：3.1 | 874 | 0.0153 | ○ | I-g |
| I-68 | I-3P | 0.14 | 0.37 | 0.76 | 0.047 | 0.013 | 0.0296 | 0.006 | 0.01 | 0.001 | 0.001 | 0.008 | 0.0001 | 0 | 0 | Ni：3.5，Bi：0.08 | 867 | 0.0218 | ○ | I-a |
| I-69 | I-3Q | 0.05 | 0.12 | 1.89 | 0.002 | 0.01 | 0.0201 | 0.001 | 0.01 | 0.001 | 0.001 | 0.000 | 0.0001 | 0.01 | 0 | Ni：0.9 | 819 | 0.0151 | ○ | I-d |
| I-70 | I-3R | 0.08 | 0.18 | 0.23 | 0.019 | 0.002 | 0.0176 | 0.011 | 0.005 | 0.001 | 0.01 | 0.000 | 0.0001 | 0 | 0 | Co：1.9，Pb：0.06 | 874 | 0.0074 | ○ | I-c |
[table 3]
| I-100 | I-4A-1 | 0.05 | 0.33 | 0.28 | 0.005 | 0.003 | 0.0214 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0.038 | - | 875 | 0.0007 | × | I-b |
| I-101 | I-4A-2 | 0.05 | 0.33 | 0.28 | 0.005 | 0.003 | 0.0214 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0.038 | - | 875 | 0.0198 | × | I-e |
| I-102 | I-4A-3 | 0.05 | 0.33 | 0.28 | 0.005 | 0.003 | 0.0214 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0.038 | - | 875 | 0.0206 | × | I-h |
| I-103 | I-4A-4 | 0.05 | 0.33 | 0.28 | 0.005 | 0.003 | 0.0214 | 0.001 | 0.001 | 0.001 | 0.001 | 0.000 | 0.0001 | 0 | 0.038 | - | 875 | 0.0208 | × | I-j |
[table 4]
| Heat treatment mode | Heating temperature (℃) | Hot-work | Speed of cooling (℃/s) | The cooling stop temperature (℃) |
| I-a | 800 | Have | 1 | 500 |
| I-b | 800 | Do not have | 1 | 450 |
| I-c | 900 | Have | 0.5 | 500 |
| I-d | 900 | Do not have | 1 | 500 |
| I-e | 1000 | Have | 0.5 | 480 |
| I-f | 1000 | Have | 5 | 500 |
| I-g | 1000 | Do not have | 1 | 500 |
| I-h | 1000 | Have | 1 | 500 |
| I-i | 1100 | Have | 1 | 430 |
| I-j | 1200 | Have | 3 | 500 |
Then, in rate of straining: 0.001～240/s, processing temperature: 20～400 ℃, rate of compression: under 20～80% the processing conditions, processing thermal analogy (formaster) testing apparatus of use capacity 200kN forges the described test film of table 1～table 3, is processed into part.Rate of straining adopts the rate of straining mean value of (in the viscous deformation) in the processing.For the part that obtains, with 20 times of live microscopes of observing multiplying power its surface is observed, confirm to have flawless.The processing conditions of each part, there are flawless and resistance to deformation to be presented in table 5～table 7.
Diameter of part) and measure number of times in addition, at load: 1000g, locate: the D/4 central part in test film cross section (D:: under 5 times the condition, use Vickers pyramid hardness testing machine to measure the Vickers' hardness (Hv) of part.The hardness of each part (Hv) is presented in table 5～table 7.
[table 5]
| Part No. | Material No. | The steel mark | Rate of straining (/s) | Processing temperature (℃) | Rate of compression (%) | Resistance to deformation (MPa) | Processing back hardness (Hv) | (3) whether formula is set up | Flawless is arranged |
| I-1 | I-1 | I-1A | 100 | 60 | 20 | 362 | 233 | ○ | Have |
| I-2 | I-2 | I-1B | 140 | 80 | 80 | 427 | 249 | ○ | Do not have |
| I-3 | I-3 | I-1C | 180 | 20 | 60 | 432 | 248 | ○ | Do not have |
| I-4 | I-4 | I-1D | 220 | 60 | 80 | 516 | 263 | ○ | Do not have |
| I-5 | I-5 | I-1E | 120 | 20 | 40 | 544 | 282 | ○ | Do not have |
| I-6 | I-6 | I-1F | 100 | 40 | 80 | 608 | 292 | ○ | Have |
| I-7 | I-7 | I-1G | 160 | 60 | 80 | 459 | 278 | ○ | Have |
| I-8 | I-8 | I-1H | 140 | 20 | 60 | 525 | 264 | ○ | Do not have |
| I-9 | I-9 | I-1I | 100 | 80 | 60 | 467 | 259 | ○ | Do not have |
| I-10 | I-10 | I-1J | 180 | 20 | 80 | 556 | 277 | ○ | Do not have |
| I-11 | I-11 | I-1K | 140 | 100 | 80 | 501 | 256 | ○ | Do not have |
| I-12 | I-12 | I-1L | 220 | 20 | 20 | 563 | 297 | ○ | Do not have |
| I-13 | I-13 | I-1M | 160 | 60 | 80 | 459 | 279 | ○ | Do not have |
| I-14 | I-14 | I-1N | 100 | 40 | 40 | 515 | 260 | ○ | Have |
| I-15 | I-15 | I-1O | 120 | 20 | 60 | 427 | 288 | ○ | Have |
| I-16 | I-16 | I-1P | 240 | 60 | 80 | 484 | 263 | ○ | Do not have |
| I-17 | I-17 | I-1Q | 200 | 80 | 20 | 500 | 254 | ○ | Do not have |
| I-18 | I-18 | I-1R | 140 | 20 | 80 | 621 | 321 | ○ | Do not have |
| I-19 | I-19 | I-1S | 180 | 20 | 20 | 488 | 321 | ○ | Do not have |
| I-20 | I-20 | I-1T | 140 | 20 | 80 | 586 | 284 | ○ | Do not have |
| I-21 | I-21 | I-1U | 100 | 20 | 20 | 537 | 293 | ○ | Do not have |
| I-22 | I-22 | I-1V | 160 | 40 | 60 | 725 | 329 | ○ | Do not have |
| I-23 | I-23 | I-1W | 220 | 20 | 40 | 703 | 305 | ○ | Do not have |
| I-24 | I-24 | I-1X | 120 | 60 | 80 | 787 | 335 | ○ | Have |
| I-25 | I-25 | I-1Y | 100 | 20 | 80 | 588 | 295 | ○ | Have |
| I-26 | I-26 | I-1Z | 140 | 80 | 80 | 555 | 329 | ○ | Have |
| I-27 | I-27 | I-2A | 200 | 20 | 20 | 557 | 270 | ○ | Have |
| I-28 | I-28 | I-2B | 100 | 40 | 80 | 548 | 268 | ○ | Have |
| I-29 | I-29 | I-2C | 160 | 20 | 20 | 547 | 243 | × | Do not have |
| I-30 | I-30 | I-2D | 180 | 20 | 60 | 622 | 271 | ○ | Do not have |
| I-31 | I-31 | I-2E | 0.001 | 20 | 80 | 681 | 301 | ○ | Have |
| I-32 | I-31 | I-2E | 0.1 | 60 | 80 | 610 | 289 | ○ | Have |
| I-33 | I-31 | I-2E | 1 | 20 | 40 | 575 | 283 | ○ | Have |
| I-34 | I-31 | I-2E | 10 | 80 | 80 | 539 | 277 | ○ | Have |
| I-35 | I-31 | I-2E | 100 | 100 | 20 | 504 | 271 | ○ | Do not have |
| I-36 | I-31 | I-2E | 200 | 200 | 60 | 493 | 270 | ○ | Do not have |
| I-37 | I-32 | I-2F | 220 | 300 | 80 | 551 | 296 | ○ | Have |
| I-38 | I-33 | I-2G | 140 | 400 | 20 | 668 | 326 | ○ | Have |
| I-39 | I-34 | I-2H | 100 | 20 | 80 | 622 | 314 | ○ | Do not have |
| I-40 | I-35 | I-2I | 160 | 20 | 80 | 483 | 305 | ○ | Do not have |
[table 6]
| Part No. | Material No. | The steel mark | Rate of straining (/s) | Processing temperature (℃) | Rate of compression (%) | Resistance to deformation (MPa) | Processing back hardness (Hv) | (3) whether formula is set up | Flawless is arranged |
| I-41 | I-36 | I-2J | 120 | 60 | 40 | 466 | 335 | ○ | Do not have |
| I-42 | I-37 | I-2K | 180 | 80 | 60 | 637 | 384 | ○ | Have |
| I-43 | I-38 | I-2L | 100 | 80 | 20 | 612 | 282 | ○ | Do not have |
| I-44 | I-39 | I-2M | 140 | 20 | 80 | 602 | 309 | ○ | Do not have |
| I-45 | I-40 | I-2N | 220 | 20 | 80 | 582 | 268 | ○ | Do not have |
| I-46 | I-41 | I-2O | 120 | 60 | 20 | 539 | 269 | ○ | Do not have |
| I-47 | I-42 | I-2P | 200 | 40 | 80 | 594 | 271 | ○ | Do not have |
| I-48 | I-43 | I-2Q | 160 | 100 | 40 | 435 | 245 | ○ | Do not have |
| I-49 | I-44 | I-2R | 100 | 20 | 20 | 551 | 282 | ○ | Do not have |
| I-50 | I-45 | I-2S | 180 | 40 | 80 | 602 | 304 | ○ | Do not have |
| I-51 | I-46 | I-2T | 100 | 20 | 60 | 541 | 280 | ○ | Do not have |
| I-52 | I-47 | I-2U | 140 | 60 | 80 | 535 | 312 | ○ | Do not have |
| I-53 | I-48 | I-2V | 200 | 20 | 40 | 513 | 261 | ○ | Do not have |
| I-54 | I-49 | I-2W | 160 | 80 | 20 | 417 | 247 | ○ | Do not have |
| I-55 | I-50 | I-2X | 220 | 20 | 40 | 502 | 267 | ○ | Do not have |
| I-56 | I-51 | I-2Y | 180 | 150 | 80 | 691 | 312 | ○ | Do not have |
| I-57 | I-52 | I-2Z | 100 | 20 | 40 | 594 | 287 | ○ | Do not have |
| I-58 | I-53 | I-3A | 120 | 40 | 60 | 564 | 300 | ○ | Do not have |
| I-59 | I-54 | I-3B | 100 | 60 | 80 | 634 | 304 | ○ | Do not have |
| I-60 | I-55 | I-3C | 160 | 20 | 80 | 527 | 278 | ○ | Do not have |
| I-61 | I-56 | I-3D | 140 | 80 | 60 | 471 | 251 | ○ | Do not have |
| I-62 | I-57 | I-3E | 200 | 20 | 80 | 598 | 299 | ○ | Do not have |
| I-63 | I-58 | I-3F | 220 | 20 | 80 | 412 | 289 | ○ | Do not have |
| I-64 | I-59 | I-3G | 100 | 150 | 20 | 597 | 339 | ○ | Do not have |
| I-65 | I-60 | I-3H | 100 | 40 | 60 | 600 | 291 | ○ | Do not have |
| I-66 | I-61 | I-3I | 180 | 60 | 40 | 593 | 305 | ○ | Do not have |
| I-67 | I-62 | I-3J | 200 | 80 | 80 | 474 | 257 | ○ | Do not have |
| I-68 | I-63 | I-3K | 100 | 20 | 40 | 578 | 291 | ○ | Do not have |
| I-69 | I-64 | I-3L | 120 | 20 | 60 | 646 | 291 | ○ | Do not have |
| I-70 | I-65 | I-3M | 180 | 20 | 80 | 576 | 316 | ○ | Do not have |
| I-71 | I-66 | I-3N | 240 | 60 | 20 | 540 | 281 | ○ | Do not have |
| I-72 | I-67 | I-3O | 140 | 20 | 60 | 618 | 298 | ○ | Do not have |
| I-73 | I-68 | I-3P | 160 | 40 | 80 | 708 | 332 | ○ | Do not have |
| I-74 | I-69 | I-3Q | 220 | 40 | 40 | 632 | 299 | ○ | Do not have |
| I-75 | I-70 | I-3R | 100 | 60 | 60 | 533 | 260 | ○ | Do not have |
| I-76 | I-71 | I-3S | 160 | 20 | 80 | 605 | 277 | ○ | Do not have |
| I-77 | I-72 | I-3T-1 | 120 | 20 | 20 | 502 | 248 | × | Do not have |
| I-78 | I-73 | I-3T-2 | 180 | 80 | 80 | 496 | 268 | ○ | Do not have |
| I-79 | I-74 | I-3T-3 | 100 | 40 | 40 | 505 | 271 | ○ | Do not have |
| I-80 | I-75 | I-3T-4 | 140 | 20 | 80 | 500 | 270 | ○ | Do not have |
[table 7]
| Part No. | Material No. | The steel mark | Rate of straining (/s) | Processing temperature (℃) | Rate of compression (%) | Resistance to deformation (MPa) | Processing back hardness (Hv) | (3) whether formula is set up | Flawless is arranged |
| I-81 | I-76 | I-3U-1 | 200 | 20 | 40 | 663 | 273 | × | Do not have |
| I-82 | I-77 | I-3U-2 | 100 | 60 | 80 | 678 | 273 | × | Do not have |
| I-83 | I-78 | I-3U-3 | 160 | 40 | 20 | 668 | 281 | ○ | Do not have |
| I-84 | I-79 | I-3U-4 | 240 | 20 | 40 | 660 | 282 | ○ | Do not have |
| I-85 | I-80 | I-3V-1 | 120 | 40 | 60 | 560 | 259 | × | Do not have |
| I-86 | I-81 | I-3V-2 | 180 | 20 | 40 | 553 | 261 | ○ | Do not have |
| I-87 | I-82 | I-3V-3 | 100 | 60 | 80 | 563 | 265 | ○ | Do not have |
| I-88 | I-83 | I-3V-4 | 140 | 20 | 20 | 557 | 282 | ○ | Do not have |
| I-89 | I-84 | I-3W-1 | 240 | 80 | 80 | 524 | 236 | × | Do not have |
| I-90 | I-85 | I-3W-2 | 160 | 40 | 60 | 531 | 239 | × | Do not have |
| I-91 | I-86 | I-3W-3 | 100 | 20 | 60 | 539 | 260 | ○ | Do not have |
| I-92 | I-87 | I-3W-4 | 120 | 40 | 80 | 536 | 274 | ○ | Do not have |
| I-93 | I-88 | I-3X-1 | 180 | 60 | 40 | 538 | 240 | × | Do not have |
| I-94 | I-89 | I-3X-2 | 160 | 20 | 20 | 540 | 241 | × | Do not have |
| I-95 | I-90 | I-3X-3 | 200 | 100 | 80 | 537 | 257 | ○ | Do not have |
| I-96 | I-91 | I-3X-4 | 140 | 20 | 20 | 543 | 259 | ○ | Do not have |
| I-97 | I-92 | I-3Y-1 | 100 | 80 | 40 | 440 | 236 | × | Do not have |
| I-98 | I-93 | I-3Y-2 | 220 | 40 | 60 | 430 | 247 | ○ | Do not have |
| I-99 | I-94 | I-3Y-3 | 120 | 60 | 80 | 438 | 248 | ○ | Do not have |
| I-100 | I-95 | I-3Y-4 | 160 | 20 | 80 | 434 | 248 | ○ | Do not have |
| I-101 | I-96 | I-3Z-1 | 180 | 100 | 20 | 481 | 230 | × | Do not have |
| I-102 | I-97 | I-3Z-2 | 240 | 20 | 80 | 477 | 235 | × | Do not have |
| I-103 | I-98 | I-3Z-3 | 140 | 20 | 40 | 486 | 275 | ○ | Do not have |
| I-104 | I-99 | I-3Z-4 | 100 | 40 | 80 | 491 | 293 | ○ | Do not have |
| I-105 | I-100 | I-4A-1 | 220 | 20 | 20 | 421 | 221 | × | Do not have |
| I-106 | I-101 | I-4A-2 | 120 | 20 | 60 | 430 | 280 | ○ | Do not have |
| I-107 | I-102 | I-4A-3 | 200 | 40 | 80 | 423 | 281 | ○ | Do not have |
| I-108 | I-103 | I-4A-4 | 160 | 60 | 40 | 426 | 282 | ○ | Do not have |
In the present embodiment, with there not being crackle on the part, with respect to part hardness, the low steel (being to satisfy following formula (3) specifically) of the resistance to deformation of steel is judged to be the cold-workability excellence.
In addition, be that part more than 240 is judged to be excellent strength with the Vickers' hardness (Hv) of part.Also have, in table 5～table 7, show whether each test film satisfies following formula (3), is designated as " zero " when satisfying formula (3), is designated as when not satisfying formula (3) " * ".
According to table 5～table 7 as can be known, under preferred processing conditions (rate of straining and processing temperature), satisfy the steel of the important document of first embodiment specified chemical composition amount of the present invention and solid solution nitrogen amount, cold-workability excellence, its excellent strength of the part that obtains thus.With respect to this, the important document of first embodiment regulation of discontented unabridged version invention, as described below, its cold-workability or part strength are poor.
Part No.I-1 (steel No.I-1A) is because the carbon amount is few, so hardness (Hv) is lower than 240, intensity is insufficient.
Part No.I-6 (steel No.I-1F) is because the carbon amount is many, so crackle takes place on the part.
Part No.I-7 (steel No.I-1G) is because the Si amount is few, so crackle takes place on the part.
Part No.I-14 (steel No.I-1N) is because the Si amount is many, so crackle takes place on the part.
Part No.I-15 (steel No.I-1O) is because the Mn amount is few, so crackle takes place on the part.
Part No.I-24 (steel No.I-1X) is because the Mn amount is many, so crackle takes place on the part.
Part No.I-25 and 26 (steel No.I-1Y and I-1Z) is because the P amount is many, so part generation crackle.
＜embodiment 2 (about the example of the present invention and the comparative example of second embodiment of the present invention) 〉
At first, the Steel Mark II-1A～II4A that constitutes by the described chemical ingredients of table 8～table 10 with the converter melting for examination steel (unit in the table is quality %), after becoming steel billet under the Continuous casting process, be rolled into the wire rod of (diameter) 12mm.Afterwards, the heat treated shown in carry out table 11.In addition, after the heat treated of the condition shown in carry out table 11, expectation is set more than 10 minutes, the preferred hold-time more than 30 minutes.
Then, the central part by the wire rod of having implemented above-mentioned heat treated cuts the test film of (diameter) 4mm * L (length) 6mm down.Also have in table 8～table 10, show also whether each test film satisfies following formula (1), is designated as " zero " when satisfying formula (1), is designated as when not satisfying " * ".In addition, " solid solution N " expression solid solution N amount in table 8～table 10, " N " represents total nitrogen.
[table 8]
| Material No. | The steel mark | Chemical constitution (quality %) | The Ac3 point (℃) | Solid solution N quality % | (1) whether formula is set up | Thermal treatment | ||||||||||||||
| C | Si | Mn | P | S | N | Al | Ti | Nb | V | Zr | B | Ta | Hf | Other | ||||||
| II-1 | II-1A | 0.13 | 0.07 | 0.15 | 0.015 | 0.015 | 0.0095 | 0.001 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 847 | 0.0081 | ○ | II-a |
| II-2 | II-1B | 0.25 | 0.17 | 0.44 | 0.009 | 0.012 | 0.0167 | 0.012 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 814 | 0.0096 | ○ | II-h |
| II-3 | II-1C | 0.34 | 0.15 | 0.32 | 0.023 | 0.028 | 0.0103 | 0.001 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 805 | 0.0089 | ○ | II-d |
| II-4 | II-1D | 0.43 | 0.12 | 0.23 | 0.018 | 0.021 | 0.0145 | 0.008 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 791 | 0.0095 | ○ | II-i |
| II-5 | II-1E | 0.56 | 0.06 | 0.14 | 0.008 | 0.008 | 0.0155 | 0.001 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 763 | 0.0141 | ○ | II-j |
| II-6 | II-1F | 0.64 | 0.06 | 0.14 | 0.008 | 0.008 | 0.0155 | 0.001 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 753 | 0.0141 | ○ | II-b |
| II-7 | II-1G | 0.46 | 0.002 | 0.27 | 0.013 | 0.012 | 0.0189 | 0.001 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 774 | 0.0175 | ○ | II-j |
| II-8 | II-1H | 0.21 | 0.18 | 0.35 | 0.006 | 0.004 | 0.0169 | 0.013 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 824 | 0.0093 | ○ | II-j |
| II-9 | II-1I | 0.19 | 0.23 | 0.10 | 0.005 | 0.032 | 0.0123 | 0.001 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 833 | 0.0109 | ○ | II-h |
| II-10 | II-1J | 0.42 | 0.38 | 0.19 | 0.007 | 0.015 | 0.0175 | 0.009 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 799 | 0.0120 | ○ | II-d |
| II-11 | II-1K | 0.26 | 0.40 | 0.13 | 0.015 | 0.008 | 0.0093 | 0.001 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 832 | 0.0079 | ○ | II-i |
| II-12 | II-1L | 0.18 | 0.57 | 0.29 | 0.009 | 0.034 | 0.0217 | 0.005 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 849 | 0.0183 | ○ | II-f |
| II-13 | II-1M | 0.54 | 0.58 | 0.41 | 0.018 | 0.013 | 0.0193 | 0.001 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 788 | 0.0179 | ○ | II-h |
| II-14 | II-1N | 0.58 | 0.62 | 0.21 | 0.009 | 0.028 | 0.0098 | 0.001 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 784 | 0.0084 | ○ | II-b |
| II-15 | II-1O | 0.16 | 0.39 | 0.03 | 0.045 | 0.041 | 0.0241 | 0.001 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 878 | 0.0227 | ○ | II-g |
| II-16 | II-1P | 0.38 | 0.17 | 0.24 | 0.019 | 0.034 | 0.0151 | 0.006 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 801 | 0.0111 | ○ | II-g |
| II-17 | II-1Q | 0.41 | 0.34 | 0.22 | 0.043 | 0.019 | 0.0087 | 0.001 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 819 | 0.0073 | ○ | II-d |
| II-18 | II-1R | 0.27 | 0.54 | 0.45 | 0.032 | 0.002 | 0.0315 | 0.015 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 844 | 0.0229 | ○ | II-e |
| II-19 | II-1S | 0.38 | 0.56 | 0.48 | 0.008 | 0.009 | 0.0316 | 0.001 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 802 | 0.0302 | ○ | II-c |
| II-20 | II-1T | 0.27 | 0.43 | 1.03 | 0.005 | 0.043 | 0.0252 | 0.023 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 806 | 0.0124 | ○ | II-j |
| II-21 | II-1U | 0.31 | 0.17 | 1.15 | 0.034 | 0.015 | 0.0197 | 0.001 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 795 | 0.0183 | ○ | II-f |
| II-22 | II-1V | 0.34 | 0.16 | 1.89 | 0.004 | 0.032 | 0.0285 | 0.015 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 751 | 0.0199 | ○ | II-b |
| II-23 | II-1W | 0.19 | 0.08 | 1.95 | 0.024 | 0.011 | 0.0144 | 0.001 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 784 | 0.0130 | ○ | II-i |
| II-24 | II-1X | 0.55 | 0.15 | 2.08 | 0.028 | 0.019 | 0.0198 | 0.001 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 724 | 0.0184 | ○ | II-h |
| II-25 | II-1Y | 0.22 | 0.35 | 0.27 | 0.060 | 0.004 | 0.0175 | 0.001 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 865 | 0.0161 | ○ | II-d |
| II-26 | II-1Z | 0.35 | 0.17 | 0.31 | 0.090 | 0.016 | 0.0307 | 0.001 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 852 | 0.0293 | ○ | II-g |
| II-27 | II-2A | 0.40 | 0.49 | 0.79 | 0.033 | 0.070 | 0.0108 | 0.001 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 804 | 0.0094 | ○ | II-a |
| II-28 | II-2B | 0.52 | 0.35 | 0.54 | 0.009 | 0.090 | 0.0108 | 0.001 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 770 | 0.0094 | ○ | II-f |
| II-29 | II-2C | 0.33 | 0.08 | 0.34 | 0.012 | 0.013 | 0.0061 | 0.008 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 799 | 0.0011 | × | II-j |
| II-30 | II-2D | 0.17 | 0.25 | 0.61 | 0.013 | 0.008 | 0.0075 | 0.001 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 829 | 0.0061 | ○ | II-e |
| II-31 | II-2E | 0.37 | 0.19 | 0.45 | 0.005 | 0.005 | 0.0195 | 0.011 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 790 | 0.0129 | ○ | II-g |
| II-32 | II-2F | 0.45 | 0.04 | 0.08 | 0.021 | 0.011 | 0.0199 | 0.001 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 789 | 0.0185 | ○ | II-h |
| II-33 | II-2G | 0.28 | 0.17 | 0.16 | 0.017 | 0.012 | 0.0256 | 0.005 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 820 | 0.0222 | ○ | II-c |
| II-34 | II-2H | 0.3 2 | 0.45 | 0.34 | 0.025 | 0.004 | 0.0218 | 0.001 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 823 | 0.0204 | ○ | II-d |
| II-35 | II-2I | 0.46 | 0.31 | 0.23 | 0.021 | 0.019 | 0.0335 | 0.014 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 800 | 0.0254 | ○ | II-f |
[table 9]
| Material No. | The steel mark | Chemical constitution (quality %) | The Ac3 point (℃) | Solid solution N quality % | (1) whether formula is set up | Thermal treatment | ||||||||||||||
| C | Si | Mn | P | S | N | Al | Ti | Nb | V | Zr | B | Ta | Hf | Other | ||||||
| II-36 | II-2J | 0.23 | 0.29 | 0.09 | 0.010 | 0.022 | 0.0376 | 0.001 | 0.001 | 0.001 | 0.001 | 1E-04 | 0.0001 | 0 | 0 | - | 831 | 0.0362 | ○ | II-1b |
| II-37 | II-2K | 0.42 | 0.25 | 1.86 | 0.008 | 0.025 | 0.0443 | 0.001 | 0.001 | 0.001 | 0.001 | 1E-04 | 0.0001 | 0 | 0 | - | 740 | 0.0429 | ○ | II-1i |
| II-38 | II-2L | 0.16 | 0.50 | 0.94 | 0.004 | 0.009 | 0.0231 | 0.001 | 0.040 | 0.001 | 0.001 | 1E-04 | 0.0001 | 0 | 0 | - | 842 | 0.0103 | ○ | II-1g |
| II-39 | II-2M | 0.57 | 0.11 | 0.75 | 0.011 | 0.032 | 0.0285 | 0.006 | 0.001 | 0.030 | 0.001 | 1E-04 | 0.0001 | 0 | 0 | - | 750 | 0.0202 | ○ | II-1i |
| II-40 | II-2N | 0.56 | 0.25 | 0.34 | 0.016 | 0.006 | 0.0229 | 0.001 | 0.001 | 0.060 | 0.020 | 1E-04 | 0.0001 | 0 | 0 | - | 773 | 0.0074 | ○ | II-1d |
| II-41 | II-2O | 0.32 | 0.38 | 0.41 | 0.023 | 0.015 | 0.0223 | 0.007 | 0.001 | 0.001 | 0.001 | 0.05 | 0.0001 | 0 | 0 | - | 819 | 0.0101 | ○ | II-1c |
| II-42 | II-2P | 0.24 | 0.05 | 0.54 | 0.039 | 0.027 | 0.0099 | 0.001 | 0.001 | 0.001 | 0.001 | 1E-04 | 0.0006 | 0 | 0 | - | 825 | 0.0079 | ○ | II-1e |
| II-43 | II-2Q | 0.19 | 0.17 | 0.13 | 0.019 | 0.005 | 0.0398 | 0.023 | 0.030 | 0.001 | 0.040 | 1E-04 | 0.0001 | 0 | 0 | - | 864 | 0.0078 | ○ | II-1h |
| II-44 | II-2R | 0.47 | 0.35 | 0.88 | 0.021 | 0.002 | 0.0308 | 0.018 | 0.001 | 0.040 | 0.001 | 0.005 | 0.0001 | 0 | 0 | - | 782 | 0.0140 | ○ | II-1f |
| II-45 | II-2S | 0.50 | 0.16 | 1.23 | 0.025 | 0.015 | 0.0155 | 0.001 | 0.001 | 0.001 | 0.030 | 0.004 | 0.0001 | 0 | 0 | - | 758 | 0.0055 | × | II-1j |
| II-46 | II-2T | 0.32 | 0.33 | 0.14 | 0.027 | 0.013 | 0.0212 | 0.009 | 0.001 | 0.001 | 0.001 | 1E-04 | 0.0001 | 0.02 | 0 | - | 829 | 0.0137 | ○ | II-1a |
| II-47 | II-2U | 0.49 | 0.28 | 0.31 | 0.038 | 0.030 | 0.0301 | 0.001 | 0.001 | 0.001 | 0.001 | 1E-04 | 0.0001 | 0 | 0.05 | - | 798 | 0.0248 | ○ | II-1c |
| II-48 | II-2V | 0.18 | 0.16 | 0.44 | 0.041 | 0.019 | 0.0232 | 0.018 | 0.001 | 0.001 | 0.001 | 1E-04 | 0.0013 | 0 | 0.03 | - | 854 | 0.0091 | ○ | II-1g |
| II-49 | II-2W | 0.39 | 0.13 | 0.30 | 0.016 | 0.044 | 0.0388 | 0.001 | 0.050 | 0.001 | 0.050 | 1E-04 | 0.0001 | 0 | 0 | - | 817 | 0.0096 | ○ | II-1i |
| II-50 | II-2X | 0.27 | 0.32 | 0.22 | 0.017 | 0.015 | 0.0342 | 0.034 | 0.001 | 0.001 | 0.001 | 0.02 | 0.0001 | 0.01 | 0 | - | 838 | 0.0116 | ○ | II-1e |
| II-51 | II-2Y | 0.24 | 0.38 | 1.53 | 0.019 | 0.009 | 0.0199 | 0.001 | 0.001 | 0.001 | 0.001 | 1E-04 | 0.0001 | 0 | 0.03 | - | 796 | 0.0162 | ○ | II-1h |
| II-52 | II-2Z | 0.47 | 0.56 | 0.09 | 0.022 | 0.018 | 0.0371 | 0.028 | 0.010 | 0.040 | 0.001 | 1E-04 | 0.0001 | 0 | 0 | - | 824 | 0.0132 | ○ | II-1b |
| II-53 | II-3A | 0.38 | 0.44 | 0.32 | 0.008 | 0.009 | 0.0233 | 0.001 | 0.010 | 0.001 | 0.001 | 1E-04 | 0.0001 | 0 | 0 | Co：4.5 | 805 | 0.0193 | ○ | II-1d |
| II-54 | II-3B | 0.32 | 0.22 | 0.43 | 0.005 | 0.045 | 0.0243 | 0.008 | 0.010 | 0.001 | 0.001 | 1E-04 | 0.0001 | 0 | 0 | Mo：0.04，Pb：0.08 | 803 | 0.0167 | ○ | II-1c |
| II-55 | II-3C | 0.27 | 0.12 | 0.12 | 0.012 | 0.019 | 0.0198 | 0.005 | 0.010 | 0.001 | 0.001 | 1E-04 | 0.0001 | 0 | 0 | Mo：1.3 | 821 | 0.0137 | ○ | II-1f |
| II-56 | II-3D | 0.19 | 0.08 | 0.65 | 0.015 | 0.003 | 0.0188 | 0.003 | 0.030 | 0.001 | 0.001 | 1E-04 | 0.0001 | 0 | 0 | W：1.8 | 829 | 0.0079 | ○ | II-1a |
| II-57 | II-3E | 0.47 | 0.09 | 0.99 | 0.009 | 0.023 | 0.0276 | 0.012 | 0.010 | 0.001 | 0.001 | 1E-04 | 0.0008 | 0 | 0 | W：0.05，Ca：0.016 | 760 | 0.0170 | ○ | II-1e |
| II-58 | II-3F | 0.54 | 0.13 | 0.15 | 0.003 | 0.019 | 0.0324 | 0.010 | 0.010 | 0.001 | 0.001 | 1E-04 | 0.0001 | 0 | 0 | Ca：0.008 | 772 | 0.0237 | ○ | II-1j |
| II-59 | II-3G | 0.28 | 0.12 | 1.22 | 0.034 | 0.039 | 0.0355 | 0.001 | 0.010 | 0.001 | 0.001 | 0.005 | 0.0001 | 0.01 | 0 | Ca：0.02，REM：0.009 | 800 | 0.0301 | ○ | II-1g |
| II-60 | II-3H | 0.23 | 0.08 | 0.56 | 0.028 | 0.011 | 0.0180 | 0.001 | 0.010 | 0.001 | 0.001 | 1E-04 | 0.0001 | 0 | 0 | REM：0.042 | 823 | 0.0140 | ○ | II-1j |
| II-61 | II-3I | 0.41 | 0.09 | 0.43 | 0.018 | 0.031 | 0.0233 | 0.001 | 0.010 | 0.001 | 0.001 | 1E-04 | 0.0001 | 0 | 0 | Mg：0.01，Cr：1.3 | 788 | 0.0193 | ○ | II-1c |
| II-62 | II-3J | 0.53 | 0.21 | 0.39 | 0.011 | 0.008 | 0.0154 | 0.004 | 0.010 | 0.001 | 0.001 | 1E-04 | 0.0001 | 0 | 0 | Li：0.005 | 773 | 0.0098 | ○ | II-1b |
| II-63 | II-3K | 0.26 | 0.39 | 0.28 | 0.032 | 0.015 | 0.0198 | 0.001 | 0.010 | 0.001 | 0.001 | 1E-04 | 0.0001 | 0 | 0 | Mg：0.013，Ca：0.003 | 842 | 0.0155 | ○ | II-1i |
| II-64 | II-3L | 0.51 | 0.43 | 0.11 | 0.008 | 0.026 | 0.0221 | 0.009 | 0.010 | 0.001 | 0.010 | 1E-04 | 0.0001 | 0 | 0 | Co：2.5.Mo：0.3 | 795 | 0.0115 | ○ | II-1f |
| II-65 | II-3M | 0.32 | 0.19 | 0.17 | 0.010 | 0.007 | 0.0308 | 0.001 | 0.010 | 0.020 | 0.001 | 1E-04 | 0.0001 | 0 | 0 | Cu：0.4 | 810 | 0.0239 | ○ | II-1e |
| II-66 | II-3N | 0.50 | 0.27 | 0.35 | 0.008 | 0.012 | 0.0203 | 0.005 | 0.010 | 0.001 | 0.001 | 1E-04 | 0.0001 | 0 | 0 | Cu：3.2，Cr：0.8 | 780 | 0.0142 | ○ | II-1e |
| II-67 | II-3O | 0.27 | 0.31 | 0.28 | 0.035 | 0.019 | 0.0198 | 0.002 | 0.010 | 0.001 | 0.001 | 1E-04 | 0.0001 | 0 | 0 | Cu：1.3，Ni：3.1 | 839 | 0.0153 | ○ | II-1g |
| II-68 | II-3P | 0.32 | 0.37 | 0.76 | 0.047 | 0.013 | 0.0296 | 0.006 | 0.010 | 0.001 | 0.001 | 0.008 | 0.0001 | 0 | 0 | Ni：3.5，Bi：0.08 | 828 | 0.0218 | ○ | II-1a |
| II-69 | II-3Q | 0.38 | 0.12 | 1.89 | 0.002 | 0.010 | 0.0201 | 0.001 | 0.010 | 0.001 | 0.001 | 1E-04 | 0.0001 | 0.01 | 0 | Ni：0.9 | 739 | 0.0151 | ○ | II-1d |
| II-70 | II-3R | 0.35 | 0.18 | 0.23 | 0.019 | 0.002 | 0.0176 | 0.011 | 0.005 | 0.001 | 0.010 | 1E-04 | 0.0001 | 0 | 0 | Co：1.9，Pb：0.06 | 812 | 0.0074 | ○ | II-1c |
[table 10]
| Material No. | The steel mark | Chemical constitution (quality %) | The Ac3 point (℃) | Solid solution N quality % | (1) whether formula is set up | Thermal treatment | ||||||||||||||
| C | Si | Mn | P | S | N | Al | Ti | Nb | V | Zr | B | Ta | Hf | Other | ||||||
| II-71 | II-3S | 0.25 | 0.05 | 0.25 | 0.036 | 0.009 | 0.0133 | 0.001 | 0.01 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | Mo：1.1 | 833 | 0.0093 | ○ | II-b |
| II-72 | II-3T | 0.45 | 0.55 | 0.11 | 0.009 | 0.01 | 0.0286 | 0.094 | 0.03 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 851 | 0.0051 | × | II-a |
| II-73 | ″ | 0.45 | 0.55 | 0.11 | 0.009 | 0.01 | 0.0286 | 0.094 | 0.03 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 0.0123 | × | II-c | |
| II-74 | ″ | 0.45 | 0.55 | 0.11 | 0.009 | 0.01 | 0.0286 | 0.094 | 0.03 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 0.0128 | × | II-e | |
| II-75 | ″ | 0.45 | 0.55 | 0.11 | 0.009 | 0.01 | 0.0286 | 0.094 | 0.03 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 0.0126 | × | II-h | |
| II-76 | II-3U | 0.19 | 0.23 | 0.94 | 0.013 | 0.022 | 0.0322 | 0.015 | 0.07 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 847 | 0.0046 | × | II-a |
| II-77 | ″ | 0.19 | 0.23 | 0.94 | 0.013 | 0.022 | 0.0322 | 0.015 | 0.07 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 0.0037 | × | II-b | |
| II-78 | ″ | 0.19 | 0.23 | 0.94 | 0.013 | 0.022 | 0.0322 | 0.015 | 0.07 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 0.0071 | × | II-i | |
| II-79 | ″ | 0.19 | 0.23 | 0.94 | 0.013 | 0.022 | 0.0322 | 0.015 | 0.07 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 0.0079 | × | II-j | |
| II-80 | II-3V | 0.31 | 0.18 | 0.43 | 0.007 | 0.009 | 0.0185 | 0.013 | 0.001 | 0.2 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 803 | 0.0056 | × | II-b |
| II-81 | ″ | 0.31 | 0.18 | 0.43 | 0.007 | 0.009 | 0.0185 | 0.013 | 0.001 | 0.2 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 0.0066 | × | II-g | |
| II-82 | ″ | 0.31 | 0.18 | 0.43 | 0.007 | 0.009 | 0.0185 | 0.013 | 0.001 | 0.2 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 0.0076 | × | II-h | |
| II-83 | ″ | 0.31 | 0.18 | 0.43 | 0.007 | 0.009 | 0.0185 | 0.013 | 0.001 | 0.2 | 0.001 | 0.0001 | 0.0001 | 0 | 0 | - | 0.0134 | × | II-i | |
| II-84 | II-3W | 0.27 | 0.47 | 0.23 | 0.021 | 0.017 | 0.0175 | 0.001 | 0.001 | 0.001 | 0.48 | 0.0001 | 0.0001 | 0 | 0 | - | 884 | 0.0001 | × | II-a |
| II-85 | ″ | 0.27 | 0.47 | 0.23 | 0.021 | 0.017 | 0.0175 | 0.001 | 0.001 | 0.001 | 0.48 | 0.0001 | 0.0001 | 0 | 0 | - | 0.0005 | × | II-d | |
| II-86 | ″ | 0.27 | 0.47 | 0.23 | 0.021 | 0.017 | 0.0175 | 0.001 | 0.001 | 0.001 | 0.48 | 0.0001 | 0.0001 | 0 | 0 | - | 0.0072 | × | II-f | |
| II-87 | ″ | 0.27 | 0.47 | 0.23 | 0.021 | 0.017 | 0.0175 | 0.001 | 0.001 | 0.001 | 0.48 | 0.0001 | 0.0001 | 0 | 0 | - | 0.0121 | × | II-i | |
| II-88 | II-3X | 0.20 | 0.05 | 0.12 | 0.018 | 0.012 | 0.0199 | 0.001 | 0.001 | 0.001 | 0.001 | 0.18 | 0.0001 | 0 | 0 | - | 831 | 0.0005 | × | II-a |
| II-89 | ″ | 0.20 | 0.05 | 0.12 | 0.018 | 0.012 | 0.0199 | 0.001 | 0.001 | 0.001 | 0.001 | 0.18 | 0.0001 | 0 | 0 | - | 0.0007 | × | II-b | |
| II-90 | ″ | 0.20 | 0.05 | 0.12 | 0.018 | 0.012 | 0.0199 | 0.001 | 0.001 | 0.001 | 0.001 | 0.18 | 0.0001 | 0 | 0 | - | 0.0062 | × | II-i | |
| II-91 | ″ | 0.20 | 0.05 | 0.12 | 0.018 | 0.012 | 0.0199 | 0.001 | 0.001 | 0.001 | 0.001 | 0.18 | 0.0001 | 0 | 0 | - | 0.0066 | × | II-j | |
| II-92 | II-3Y | 0.38 | 0.19 | 0.08 | 0.007 | 0.047 | 0.0099 | 0.012 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0014 | 0 | 0 | - | 801 | 0.0045 | × | II-b |
| II-93 | ″ | 0.38 | 0.19 | 0.08 | 0.007 | 0.047 | 0.0099 | 0.012 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0014 | 0 | 0 | - | 0.0089 | × | II-e | |
| II-94 | ″ | 0.38 | 0.19 | 0.08 | 0.007 | 0.047 | 0.0099 | 0.012 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0014 | 0 | 0 | - | 0.0089 | × | II-g | |
| II-95 | ″ | 0.38 | 0.19 | 0.08 | 0.007 | 0.047 | 0.0099 | 0.012 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0014 | 0 | 0 | - | 0.0091 | × | II-i | |
| II-96 | II-3Z | 0.51 | 0.09 | 0.19 | 0.032 | 0.022 | 0.0221 | 0.035 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0.038 | 0 | - | 800 | 0.0005 | × | II-a |
| II-97 | ″ | 0.51 | 0.09 | 0.19 | 0.032 | 0.022 | 0.0221 | 0.035 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0.038 | 0 | - | 0.0022 | × | II-b | |
| Il-98 | ″ | 0.51 | 0.09 | 0.19 | 0.032 | 0.022 | 0.0221 | 0.035 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0.038 | 0 | - | 0.0151 | × | II-h | |
| II-99 | ″ | 0.51 | 0.09 | 0.19 | 0.032 | 0.022 | 0.0221 | 0.035 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0.038 | 0 | - | 0.0208 | × | II-i | |
| II-100 | II-4A | 0.35 | 0.33 | 0.28 | 0.005 | 0.003 | 0.0214 | 0.032 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0.038 | - | 800 | 0.0007 | × | II-b |
| II-101 | ″ | 0.35 | 0.33 | 0.28 | 0.005 | 0.003 | 0.0214 | 0.032 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0.038 | - | 0.0198 | × | II-e | |
| II-102 | ″ | 0.35 | 0.33 | 0.28 | 0.005 | 0.003 | 0.0214 | 0.032 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0.038 | - | 0.0206 | × | II-h | |
| II-103 | ″ | 0.35 | 0.33 | 0.28 | 0.005 | 0.003 | 0.0214 | 0.032 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.0001 | 0 | 0.038 | - | 0.0208 | × | II-j |
[table 11]
| Heat treatment mode | Heating temperature (℃) | Hot-work | Speed of cooling (℃/s) | The cooling stop temperature (℃) |
| II-a | 800 | Have | 5 | 500 |
| II-b | 800 | Do not have | 5 | 450 |
| II-c | 900 | Have | 5 | 500 |
| II-d | 900 | Do not have | 5 | 500 |
| II-e | 1000 | Have | 0.5 | 480 |
| II-f | 1000 | Have | 1 | 500 |
| II-g | 1000 | Do not have | 5 | 500 |
| II-h | 1000 | Have | 5 | 500 |
| II-i | 1100 | Have | 1 | 430 |
| II-j | 1200 | Have | 3 | 500 |
Then, processing rate of straining: 0.001～240/s, processing temperature: 20～400 ℃, rate of compression: under 20～80% the processing conditions, processing thermal analogy (formaster) testing apparatus of use capacity 200kN forges the described test film of table 8～table 10, is processed into part.Rate of straining adopts the rate of straining mean value of (in the viscous deformation) in the processing.
For the part that obtains, adopt stereomicroscope, observe the surface with 20 times observation multiplying powers.The processing conditions of each part, there are flawless and resistance to deformation to be presented in table 12～table 14.
Diameter of part) and measure number of times in addition, at load: 1000g, locate: the D/4 central part in test film cross section (D:: under 5 times the condition, use Vickers pyramid hardness testing machine to measure the Vickers' hardness (Hv) of part.The hardness of each part (Hv) is presented in table 12～table 14.
[table 12]
| Part No. | Material No. | The steel mark | Rate of straining (/s) | Processing temperature (℃) | Rate of compression (%) | Resistance to deformation (MPa) | Processing back hardness (Hv) | Flawless is arranged | (3) whether formula is set up |
| II-1 | II-1 | II-1A | 100 | 60 | 20 | 390 | 234 | Do not have | ○ |
| II-2 | II-2 | II-1B | 140 | 80 | 80 | 671 | 282 | Do not have | ○ |
| II-3 | II-3 | II-1C | 180 | 20 | 60 | 643 | 277 | Do not have | ○ |
| II-4 | II-4 | II-1D | 220 | 60 | 80 | 697 | 286 | Do not have | ○ |
| II-5 | II-5 | II-1E | 120 | 20 | 40 | 905 | 326 | Do not have | ○ |
| II-6 | II-6 | II-1F | 100 | 40 | 80 | 1019 | 345 | Have | ○ |
| II-7 | II-7 | II-1G | 160 | 60 | 80 | 807 | 313 | Have | ○ |
| II-8 | II-8 | II-1H | 140 | 20 | 60 | 548 | 261 | Do not have | ○ |
| II-9 | II-9 | II-1I | 100 | 80 | 60 | 614 | 274 | Do not have | ○ |
| II-10 | II-10 | II-1J | 180 | 20 | 80 | 727 | 294 | Do not have | ○ |
| II-11 | II-11 | II-1K | 140 | 100 | 80 | 687 | 283 | Do not have | ○ |
| II-12 | II-12 | II-1L | 220 | 20 | 20 | 416 | 248 | Do not have | ○ |
| II-13 | II-13 | II-1M | 160 | 60 | 80 | 952 | 337 | Do not have | ○ |
| II-14 | II-14 | II-1N | 100 | 40 | 40 | 1035 | 342 | Have | ○ |
| II-15 | II-15 | II-1O | 120 | 20 | 60 | 486 | 264 | Have | ○ |
| II-16 | II-16 | II-1P | 240 | 60 | 80 | 622 | 275 | Do not have | ○ |
| II-17 | II-17 | II-1Q | 200 | 80 | 20 | 746 | 292 | Do not have | ○ |
| II-18 | II-18 | II-1R | 140 | 20 | 80 | 674 | 296 | Do not have | ○ |
| II-19 | II-19 | II-1S | 180 | 20 | 20 | 740 | 314 | Do not have | ○ |
| II-20 | II-20 | II-1T | 140 | 20 | 80 | 734 | 295 | Do not have | ○ |
| II-21 | II-21 | II-1U | 100 | 20 | 20 | 828 | 317 | Do not have | ○ |
| II-22 | II-22 | II-1V | 160 | 40 | 60 | 881 | 327 | Do not have | ○ |
| II-23 | II-23 | II-1W | 220 | 20 | 40 | 585 | 271 | Do not have | ○ |
| II-24 | II-24 | II-1X | 120 | 60 | 80 | 1182 | 376 | Have | ○ |
| II-25 | II-25 | II-1Y | 100 | 20 | 80 | 628 | 282 | Have | ○ |
| II-26 | II-26 | II-1Z | 140 | 80 | 80 | 770 | 318 | Have | ○ |
| II-27 | II-27 | II-2A | 200 | 20 | 20 | 760 | 297 | Have | ○ |
| II-28 | II-28 | II-2B | 100 | 40 | 80 | 998 | 336 | Have | ○ |
| II-29 | II-29 | II-2C | 160 | 20 | 20 | 652 | 271 | Do not have | × |
| II-30 | II-30 | II-2D | 180 | 20 | 60 | 468 | 245 | Do not have | ○ |
| II-31 | II-31 | II-2E | 0.001 | 20 | 80 | 960 | 334 | Have | ○ |
| II-32 | ″ | ″ | 0.1 | 60 | 80 | 1000 | 340 | Have | ○ |
| II-33 | ″ | ″ | 1 | 20 | 40 | 958 | 333 | Have | ○ |
| II-34 | ″ | ″ | 10 | 80 | 80 | 1005 | 341 | Have | ○ |
| II-35 | ″ | ″ | 100 | 100 | 20 | 890 | 322 | Do not have | ○ |
| II-36 | ″ | ″ | 200 | 200 | 60 | 840 | 314 | Do not have | ○ |
| II-37 | II-32 | II-2F | 220 | 300 | 80 | 928 | 334 | Have | ○ |
| II-38 | II-33 | II-2G | 140 | 400 | 20 | 993 | 348 | Have | ○ |
| II-39 | II-34 | II-2H | 100 | 20 | 80 | 768 | 309 | Do not have | ○ |
| II-40 | II-35 | II-2I | 160 | 20 | 80 | 793 | 318 | Do not have | ○ |
[table 13]
| Part No. | Material No. | The steel mark | Rate of straining (/s) | Processing temperature (℃) | Rate of compression (%) | Resistance to deformation (MPa) | Processing back hardness (Hv) | Flawless is arranged | (3) whether formula is set up |
| II-41 | II-36 | II-2J | 120 | 60 | 40 | 624 | 301 | Do not have | ○ |
| II-42 | II-37 | II-2K | 180 | 80 | 60 | 978 | 367 | Have | ○ |
| II-43 | II-38 | II-2L | 100 | 80 | 20 | 703 | 288 | Do not have | ○ |
| II-44 | II-39 | II-2M | 140 | 20 | 80 | 966 | 342 | Do not have | ○ |
| II-45 | II-40 | II-2N | 220 | 20 | 80 | 807 | 303 | Do not have | ○ |
| II-46 | II-41 | II-2O | 120 | 60 | 20 | 786 | 302 | Do not have | ○ |
| II-47 | II-42 | II-2P | 200 | 40 | 80 | 528 | 256 | Do not have | ○ |
| II-48 | II-43 | II-2Q | 160 | 100 | 40 | 551 | 260 | Do not have | ○ |
| II-49 | II-44 | II-2R | 100 | 20 | 20 | 981 | 338 | Do not have | ○ |
| II-50 | II-45 | II-2S | 180 | 40 | 80 | 929 | 321 | Do not have | × |
| II-51 | II-46 | II-2T | 100 | 20 | 60 | 735 | 297 | Do not have | ○ |
| II-52 | II-47 | II-2U | 140 | 60 | 80 | 903 | 336 | Do not have | ○ |
| II-53 | II-48 | II-2V | 200 | 20 | 40 | 429 | 241 | Do not have | ○ |
| II-54 | II-49 | II-2W | 160 | 80 | 20 | 788 | 302 | Do not have | ○ |
| II-55 | II-50 | II-2X | 220 | 20 | 40 | 508 | 257 | Do not have | ○ |
| II-56 | II-51 | II-2Y | 180 | 150 | 80 | 825 | 314 | Do not have | ○ |
| II-57 | II-52 | II-2Z | 100 | 20 | 40 | 906 | 325 | Do not have | ○ |
| II-58 | II-53 | II-3A | 120 | 40 | 60 | 878 | 326 | Do not have | ○ |
| II-59 | II-54 | II-3B | 100 | 60 | 80 | 856 | 320 | Do not have | ○ |
| II-60 | II-55 | II-3C | 160 | 20 | 80 | 620 | 278 | Do not have | ○ |
| II-61 | II-56 | II-3D | 140 | 80 | 60 | 668 | 280 | Do not have | ○ |
| II-62 | II-57 | II-3E | 200 | 20 | 80 | 872 | 323 | Do not have | ○ |
| II-63 | II-58 | II-3F | 220 | 20 | 80 | 806 | 319 | Do not have | ○ |
| II-64 | II-59 | II-3G | 100 | 150 | 20 | 988 | 355 | Do not have | ○ |
| II-65 | II-60 | II-3H | 100 | 40 | 60 | 729 | 296 | Do not have | ○ |
| II-66 | II-61 | II-3I | 180 | 60 | 40 | 817 | 316 | Do not have | ○ |
| II-67 | II-62 | II-3J | 200 | 80 | 80 | 923 | 324 | Do not have | ○ |
| II-68 | II-63 | II-3K | 100 | 20 | 40 | 744 | 300 | Do not have | ○ |
| II-69 | II-64 | II-3L | 120 | 20 | 60 | 955 | 331 | Do not have | ○ |
| II-70 | II-65 | II-3M | 180 | 20 | 80 | 663 | 295 | Do not have | ○ |
| II-71 | II-66 | II-3N | 240 | 60 | 20 | 818 | 311 | Do not have | ○ |
| II-72 | II-67 | II-3O | 140 | 20 | 60 | 688 | 291 | Do not have | ○ |
| II-73 | II-68 | II-3P | 160 | 40 | 80 | 802 | 316 | Do not have | ○ |
| II-74 | II-69 | II-3Q | 220 | 40 | 40 | 889 | 324 | Do not have | ○ |
| II-75 | II-70 | II-3R | 100 | 60 | 60 | 860 | 311 | Do not have | ○ |
| II-76 | II-71 | II-3S | 160 | 20 | 80 | 604 | 271 | Do not have | ○ |
| II-77 | II-72 | II-3T | 120 | 20 | 20 | 860 | 305 | Do not have | × |
| II-78 | II-73 | ″ | 180 | 80 | 80 | 830 | 311 | Do not have | ○ |
| II-79 | II-74 | ″ | 100 | 40 | 40 | 910 | 325 | Do not have | ○ |
| II-80 | II-75 | ″ | 140 | 20 | 80 | 830 | 312 | Do not have | ○ |
[table 14]
| Part No. | Material No. | The steel mark | Rate of straining (/s) | Processing temperature (℃) | Rate of compression (%) | Resistance to deformation (MPa) | Processing back hardness (Hv) | Flawless is arranged | (3) whether formula is set up |
| II-81 | II-76 | II-3U | 200 | 20 | 40 | 515 | 247 | Do not have | × |
| II-82 | II-77 | ″ | 100 | 60 | 80 | 705 | 278 | Do not have | × |
| II-83 | II-78 | ″ | 160 | 40 | 20 | 596 | 267 | Do not have | ○ |
| II-84 | II-79 | ″ | 240 | 20 | 40 | 456 | 245 | Do not have | ○ |
| II-85 | II-80 | II-3V | 120 | 40 | 60 | 757 | 288 | Do not have | × |
| II-86 | II-81 | ″ | 180 | 20 | 40 | 647 | 275 | Do not have | ○ |
| II-87 | II-82 | ″ | 100 | 60 | 80 | 807 | 303 | Do not have | ○ |
| II-88 | II-83 | ″ | 140 | 20 | 20 | 707 | 292 | Do not have | ○ |
| II-89 | II-84 | II-3W | 240 | 80 | 80 | 609 | 258 | Do not have | × |
| II-90 | II-85 | ″ | 160 | 40 | 60 | 689 | 272 | Do not have | × |
| II-91 | II-86 | ″ | 100 | 20 | 60 | 759 | 294 | Do not have | ○ |
| II-92 | II-87 | ″ | 120 | 40 | 80 | 750 | 298 | Do not have | ○ |
| II-93 | II-88 | II-3X | 180 | 60 | 40 | 495 | 240 | Do not have | × |
| II-94 | II-89 | ″ | 160 | 20 | 20 | 485 | 238 | Do not have | × |
| II-95 | II-90 | ″ | 200 | 100 | 80 | 505 | 251 | Do not have | ○ |
| II-96 | II-91 | ″ | 140 | 20 | 20 | 515 | 253 | Do not have | ○ |
| II-97 | II-92 | II-3Y | 100 | 80 | 40 | 835 | 300 | Do not have | × |
| II-98 | II-93 | ″ | 220 | 40 | 60 | 615 | 272 | Do not have | ○ |
| II-99 | II-94 | ″ | 120 | 60 | 80 | 785 | 300 | Do not have | ○ |
| II-100 | II-95 | ″ | 160 | 20 | 80 | 685 | 284 | Do not have | ○ |
| II-101 | II-96 | II-3Z | 180 | 100 | 20 | 866 | 302 | Do not have | × |
| II-102 | II-97 | ″ | 240 | 20 | 80 | 696 | 275 | Do not have | × |
| II-103 | II-98 | ″ | 140 | 20 | 40 | 847 | 317 | Do not have | ○ |
| II-104 | II-99 | ″ | 100 | 40 | 80 | 927 | 336 | Do not have | ○ |
| II-105 | II-100 | II-4A | 220 | 20 | 20 | 605 | 258 | Do not have | × |
| II-106 | II-101 | ″ | 120 | 20 | 60 | 756 | 307 | Do not have | ○ |
| II-107 | II-102 | ″ | 200 | 40 | 80 | 656 | 291 | Do not have | ○ |
| II-108 | II-103 | ″ | 160 | 60 | 40 | 736 | 304 | Do not have | ○ |
In the present embodiment, part does not have crackle, is judged to be the steel low with respect to the resistance to deformation of part hardness steel (specifically, satisfying following formula (3)), the cold-workability excellence.In addition, as necessary part strength, its condition is that Vickers' hardness (Hv) is more than 240.
Also have, in table 12～table 14, show also whether each test film satisfies following formula (3), is designated as " zero " when satisfying formula (3), is designated as when not satisfying formula (3) " * ".
By table 12～table 14 as can be known, under preferred processing conditions (rate of straining and processing temperature), satisfy the steel of the important document of specified chemical composition amount of the present invention and solid solution nitrogen amount, the cold-workability excellence, crackle does not take place in the part that obtains thus, the part strength excellence.
With respect to this, discontented unabridged version invention regulation important document, as described below, crackle can take place, or does not satisfy the balanced differences of its cold-workability of formula (3) and part hardness.
Part No.II-1 has been to use C to measure the example of the Steel Mark II-1A of the specialized range that is lower than second embodiment of the present invention, and the hardness after the processing does not reach the scope of regulation.
Part No.II-6 has been to use C to measure the example of the Steel Mark II-1F of the specialized range that is higher than second embodiment of the present invention, and crackle has taken place on the part.
Part No.II-7 has been to use Si to measure the example of the steel ticket label II-1G of the specialized range that is lower than second embodiment of the present invention, and crackle has taken place on the part.
Part No.II-14 has been to use Si to measure the example of the Steel Mark II-1N of the specialized range that is higher than second embodiment of the present invention, and crackle has taken place on the part.
Part No.II-15 has been to use Mn to measure the example of the Steel Mark II-1O of the specialized range that is lower than second embodiment of the present invention, and crackle has taken place on the part.
Part No.II-24 has been to use Mn to measure the example of the Steel Mark II-1X of the specialized range that is higher than second embodiment of the present invention, and crackle has taken place on the part.
Part No.II-25 and No.II-26 have been to use P to measure the Steel Mark II-1Y of the specialized range that is higher than second embodiment of the present invention and the example of II-1Z, and crackle has taken place.
Part No.II-27 and part No.II-28 have been to use S to measure the Steel Mark II-2A of the specialized range that is higher than second embodiment of the present invention and the example of II-2B, and crackle has taken place.
Part No.II-29 has been to use N to measure the example of the Steel Mark II-2C of the preferable range (more than 0.007%) that is lower than second embodiment of the present invention, because solid solution N amount is lacked than the specialized range of second embodiment of the present invention, so the balanced differences of cold-workability and hardness.That is, do not satisfy following formula (3).
Part No.II-42 has been to use N to measure the example of the Steel Mark II-2K of the specialized range that is lower than second embodiment of the present invention, and crackle has taken place.
Part No.II-31～II-34, though employing chemical ingredients amount satisfies the steel of the Steel Mark II-2E of second embodiment regulation of the present invention, slow because high speed cold adds the rate of straining in man-hour, so dynamic strain aging takes place, there is crackle to take place.
Part No.II-37～II-38, though employing chemical ingredients amount satisfies the steel of the Steel Mark II-2F～II-2G of second embodiment regulation of the present invention,,,, have crackle to take place so dynamic strain aging takes place because high speed cold adds the temperature height in man-hour.
The pairing Steel Mark II-2S of part No.II-50 is not because satisfy formula (1), so solid solution N amount is lacked (table 9) than specified amount.Therefore, the balanced differences of its cold-workability of part No.II-50 and hardness (not satisfying formula (3)).But, even under the situation that does not satisfy formula (1), method according to heat treatment mode, also there is solid solution N amount to satisfy situation (for example, material No.II-73～II-75, the No.II-78～II-79 of table 10, No.II-81～II-83, No.II-86～II-87, No.II-90～II-91, No.II-93～II-95, No.II-98～II-99, the No.II-101～II-103) of the specialized range of second embodiment of the present invention.
The chemical ingredients amount that is to use part No.II-77, part No.II-81～II-82, part No.II-85, part No.II-89～II-90, part No.II-93～II-94, part No.II-97, part No.II-101～II-102, part No.II-105 satisfies the Steel Mark II-2S of the regulation of second embodiment of the present invention, and the example of the steel of II-3T～II-4A, but, (adaptability of the heat treatment mode II-a of table 11～II-j) is not agreed with, so the solid solution N that can not get stipulating amount because with creating conditions of using respectively.Consequently do not satisfy formula (3).That is the balanced differences of cold-workability and part hardness.
＜embodiment 3 (about the example of the present invention and the comparative example of the 3rd embodiment of the present invention) 〉
At first, Steel Mark III-1A～the III3S that constitutes by table 15 and the described chemical ingredients of table 16 (unit is quality %) with the converter melting for the examination steel (for convenience, record and narrate aftermentioned in the lump by the numbering of cold worked part), after becoming steel billet under the Continuous casting process, be rolled into the wire rod of (diameter) 12mm.Afterwards, carry out wire rod heating → (hot-work) → such thermal treatment of cooling.This thermal treatment is shown in table 17, carries out with the pattern of III-a～III-j.In addition, after the heat treated of the condition shown in carry out table 17, expectation is set more than 10 minutes, the preferred hold-time more than 30 minutes.
Then, the central part by the wire rod of having implemented above-mentioned heat treated cuts the test film of (diameter) 4mm * L (length) 6mm down.
" N " expression total nitrogen (quality %) in table 15 and the table 16, " solid solution N " expression solid solution N amount (quality %), " N compound " expression N compound amount " quality % ".Solid solution N amount as above-mentioned according to JIS G 1228, deducts N compound amount by the total N content from steel and calculates.
[table 15]
| Steel mark/III-part No | Chemical constitution (quality %) | Solid solution N (quality %) | N compound (quality %) | Thermal treatment | ||||||||||||||
| C | Si | Mn | P | S | N | Al | Ti | Nb | V | Zr | B | Ta | Hf | Other | ||||
| III-1A/III-1 | 0.01 | 0.10 | 0.17 | 0.018 | 0.020 | 0.0107 | 0.0008 | 0.0017 | 0.0007 | 0.0007 | 0.0009 | 0.00008 | 0.00006 | 0.00005 | - | 0.0093 | 0.0014 | III-a |
| III-1B/III-2 | 0.07 | 0.16 | 0.49 | 0.008 | 0.015 | 0.0133 | 0.0009 | 0.0007 | 0.0007 | 0.0008 | 0.0009 | 0.00008 | 0.00006 | 0.00005 | - | 0.0121 | 0.0012 | III-h |
| III-1C/III-3 | 0.12 | 0.13 | 0.34 | 0.025 | 0.030 | 0.0092 | 0.0009 | 0.0016 | 0.0007 | 0.0007 | 0.0009 | 0.00008 | 0.00008 | 0.00005 | - | 0.0077 | 0.0015 | III-c |
| III-1D/III-4 | 0.25 | 0.09 | 0.24 | 0.023 | 0.022 | 0.0119 | 0.0008 | 0.0017 | 0.0007 | 0.0007 | 0.0008 | 0.00009 | 0.00008 | 0.00005 | - | 0.0105 | 0.0014 | III-g |
| III-1E/III-5 | 0.51 | 0.02 | 0.12 | 0.005 | 0.010 | 0.0130 | 0.0007 | 0.0009 | 0.0007 | 0.0006 | 0.0008 | 0.00009 | 0.00008 | 0.00005 | - | 0.0119 | 0.0011 | III-j |
| III-1F/III-6 | 0.64 | 0.08 | 0.16 | 0.012 | 0.013 | 0.0124 | 0.0006 | 0.0017 | 0.0008 | 0.0007 | 0.0009 | 0.00009 | 0.00007 | 0.00006 | - | 0.0110 | 0.0014 | III-f |
| III-1G/III-7 | 0.12 | 0.003 | 0.24 | 0.012 | 0.014 | 0.0138 | 0.0006 | 0.0017 | 0.0007 | 0.0006 | 0.0008 | 0.00009 | 0.00006 | 0.00006 | - | 0.0124 | 0.0013 | III-a |
| III-1H/III-8 | 0.08 | 0.19 | 0.39 | 0.010 | 0.005 | 0.0138 | 0.0006 | 0.0018 | 0.0007 | 0.0005 | 0.0008 | 0.00009 | 0.00006 | 0.00005 | - | 0.0124 | 0.0013 | III-j |
| III-1I/III-9 | 0.14 | 0.25 | 0.13 | 0.006 | 0.030 | 0.0097 | 0.0006 | 0.0011 | 0.0006 | 0.0005 | 0.0009 | 0.00009 | 0.00006 | 0.00005 | - | 0.0085 | 0.0011 | III-b |
| III-1J/III-10 | 0.21 | 0.43 | 0.17 | 0.012 | 0.017 | 0.0124 | 0.0007 | 0.0017 | 0.0006 | 0.0006 | 0.0009 | 0.00008 | 0.00006 | 0.00004 | - | 0.0110 | 0.0014 | III-i |
| III-1K/III-11 | 0.19 | 0.39 | 0.12 | 0.016 | 0.005 | 0.0123 | 0.0007 | 0.0012 | 0.0006 | 0.0006 | 0.0009 | 0.00008 | 0.00007 | 0.00004 | - | 0.0111 | 0.0012 | III-i |
| III-1L/III-12 | 0.28 | 0.51 | 0.26 | 0.014 | 0.038 | 0.0156 | 0.0007 | 0.0017 | 0.0007 | 0.0006 | 0.0009 | 0.00009 | 0.00007 | 0.00003 | - | 0.0142 | 0.0014 | III-g |
| III-1M/III-13 | 0.07 | 0.58 | 0.44 | 0.021 | 0.016 | 0.0144 | 0.0007 | 0.0017 | 0.0007 | 0.0007 | 0.0008 | 0.00008 | 0.00008 | 0.00006 | - | 0.0130 | 0.0014 | III-h |
| III-1N/III-14 | 0.31 | 0.65 | 0.20 | 0.019 | 0.026 | 0.0096 | 0.0007 | 0.0013 | 0.0007 | 0.0007 | 0.0007 | 0.00008 | 0.00008 | 0.00006 | - | 0.0083 | 0.0013 | III-f |
| III-1O/III-15 | 0.08 | 0.37 | 0.01 | 0.043 | 0.040 | 0.0168 | 0.0007 | 0.0017 | 0.0008 | 0.0007 | 0.0007 | 0.00009 | 0.00007 | 0.00005 | - | 0.0154 | 0.0014 | III-g |
| III-1P/III-16 | 0.21 | 0.21 | 0.21 | 0.018 | 0.031 | 0.0106 | 0.0008 | 0.0017 | 0.0008 | 0.0008 | 0.0007 | 0.00009 | 0.00007 | 0.00006 | - | 0.0091 | 0.0015 | III-g |
| III-1Q/III-17 | 0.23 | 0.37 | 0.18 | 0.040 | 0.022 | 0.0098 | 0.0008 | 0.0017 | 0.0008 | 0.0008 | 0.0007 | 0.00009 | 0.00008 | 0.00006 | - | 0.0083 | 0.0015 | III-d |
| III-1R/III-18 | 0.32 | 0.53 | 0.47 | 0.028 | 0.002 | 0.0236 | 0.0008 | 0.0006 | 0.0008 | 0.0008 | 0.0007 | 0.00009 | 0.00007 | 0.00006 | - | 0.0225 | 0.0012 | IIIie |
| III-1S/III-19 | 0.12 | 0.58 | 0.52 | 0.006 | 0.012 | 0.0234 | 0.0008 | 0.0019 | 0.0008 | 0.0009 | 0.0008 | 0.00008 | 0.00007 | 0.00006 | - | 0.0218 | 0.0016 | III-j |
| III-1T/III-20 | 0.17 | 0.48 | 1.04 | 0.007 | 0.042 | 0.0176 | 0.0006 | 0.0019 | 0.0007 | 0.0009 | 0.0008 | 0.00007 | 0.00007 | 0.00007 | - | 0.0162 | 0.0014 | III-j |
| III-1U/III-21 | 0.15 | 0.14 | 1.17 | 0.031 | 0.017 | 0.0144 | 0.0007 | 0.0019 | 0.0007 | 0.0009 | 0.0008 | 0.00007 | 0.00007 | 0.00008 | - | 0.0129 | 0.0015 | III-h |
| III-1V/III-22 | 0.45 | 0.20 | 1.54 | 0.003 | 0.037 | 0.0214 | 0.0007 | 0.0019 | 0.0007 | 0.0009 | 0.0008 | 0.00007 | 0.00006 | 0.00008 | - | 0.0199 | 0.0015 | III-g |
| III-1W/III-23 | 0.33 | 0.07 | 1.94 | 0.027 | 0.008 | 0.0116 | 0.0007 | 0.0018 | 0.0007 | 0.0009 | 0.0008 | 0.00007 | 0.00006 | 0.00007 | - | 0.0101 | 0.0015 | III-d |
| III-1X/III-24 | 0.56 | 0.19 | 2.07 | 0.030 | 0.023 | 0.0144 | 0.0007 | 0.0008 | 0.0007 | 0.0008 | 0.0008 | 0.00007 | 0.00005 | 0.00007 | - | 0.0133 | 0.0011 | III-h |
| III-1Y/III-25 | 0.34 | 0.36 | 0.29 | 0.063 | 0.003 | 0.0142 | 0.0008 | 0.0018 | 0.0007 | 0.0008 | 0.0008 | 0.00008 | 0.00005 | 0.00007 | - | 0.0127 | 0.0015 | III-e |
| III-1Z/III-26 | 0.25 | 0.19 | 0.34 | 0.091 | 0.020 | 0.0221 | 0.0008 | 0.0018 | 0.0007 | 0.0008 | 0.0007 | 0.00008 | 0.00006 | 0.00006 | - | 0.0206 | 0.0015 | III-f |
| III-2A/III-27 | 0.26 | 0.54 | 0.77 | 0.026 | 0.071 | 0.0107 | 0.0007 | 0.0019 | 0.0007 | 0.0007 | 0.0008 | 0.00008 | 0.00006 | 0.00006 | - | 0.0093 | 0.0014 | III-j |
| III-2B/III-28 | 0.22 | 0.37 | 0.58 | 0.014 | 0.095 | 0.0088 | 0.0008 | 0.0018 | 0.0008 | 0.0007 | 0.0008 | 0.00008 | 0.00006 | 0.00007 | - | 0.0073 | 0.0015 | III-b |
| III-2C/III-29 | 0.19 | 0.09 | 0.37 | 0.015 | 0.014 | 0.0057 | 0.0007 | 0.0018 | 0.0007 | 0.0006 | 0.0008 | 0.00008 | 0.00007 | 0.00007 | - | 0.0043 | 0.0014 | III-i |
| III-2D/III-30 | 0.27 | 0.23 | 0.60 | 0.015 | 0.013 | 0.0082 | 0.0008 | 0.0018 | 0.0008 | 0.0006 | 0.0008 | 0.00008 | 0.00007 | 0.00007 | - | 0.0067 | 0.0015 | III-d |
| III-2E/III-31-36 | 0.13 | 0.21 | 0.47 | 0.006 | 0.008 | 0.0139 | 0.0007 | 0.0018 | 0.0008 | 0.0006 | 0.0008 | 0.00008 | 0.00007 | 0.00007 | - | 0.0125 | 0.0014 | III-g |
| III-2F/III-37 | 0.22 | 0.01 | 0.13 | 0.023 | 0.021 | 0.0154 | 0.0007 | 0.0017 | 0.0007 | 0.0006 | 0.0009 | 0.00007 | 0.00007 | 0.00007 | - | 0.0141 | 0.0014 | III-g |
| III-2G/III-38 | 0.33 | 0.21 | 0.13 | 0.022 | 0.010 | 0.0185 | 0.0007 | 0.0017 | 0.0007 | 0.0005 | 0.0009 | 0.00008 | 0.00007 | 0.00007 | - | 0.0172 | 0.0013 | III-f |
| III-2H/III-39 | 0.32 | 0.48 | 0.38 | 0.027 | 0.003 | 0.0169 | 0.0007 | 0.0017 | 0.0007 | 0.0007 | 0.0008 | 0.00008 | 0.00006 | 0.00007 | - | 0.0155 | 0.0014 | III-c |
| III-2I/III-40 | 0.24 | 0.29 | 0.22 | 0.022 | 0.016 | 0.0249 | 0.0007 | 0.0018 | 0.0008 | 0.0007 | 0.0008 | 0.00008 | 0.00006 | 0.00007 | - | 0.0234 | 0.0014 | III-f |
| III-2J/III-41 | 0.09 | 0.28 | 0.13 | 0.008 | 0.018 | 0.0271 | 0.0007 | 0.0017 | 0.0009 | 0.0006 | 0.0008 | 0.00008 | 0.00006 | 0.00006 | - | 0.0257 | 0.0014 | III-b |
| III-2K/III-42 | 0.32 | 0.22 | 1.87 | 0.010 | 0.023 | 0.0413 | 0.0007 | 0.0016 | 0.0009 | 0.0006 | 0.0007 | 0.00008 | 0.00006 | 0.00006 | - | 0.0400 | 0.0013 | III-i |
| III-2L/III-43 | 0.30 | 0.55 | 0.99 | 0.001 | 0.011 | 0.0163 | 0.0007 | 0.0016 | 0.0009 | 0.0007 | 0.0007 | 0.00009 | 0.00006 | 0.00006 | - | 0.0150 | 0.0014 | III-d |
| III-2M/III-44 | 0.31 | 0.12 | 0.76 | 0.015 | 0.029 | 0.0220 | 0.0007 | 0.0016 | 0.0009 | 0.0007 | 0.0008 | 0.00009 | 0.00006 | 0.00006 | - | 0.0206 | 0.0014 | III-j |
| III-2N/III-45 | 0.28 | 0.30 | 0.39 | 0.019 | 0.005 | 0.0162 | 0.0008 | 0.0010 | 0.0008 | 0.0007 | 0.0008 | 0.00008 | 0.00006 | 0.00007 | - | 0.0149 | 0.0012 | III-g |
[table 16]
| Steel mark/part No | Chemical constitution (quality %) | Solid solution N (quality %) | N compound (quality %) | Thermal treatment | ||||||||||||||
| C | Si | Mn | P | S | N | Al | Ti | Nb | V | Zr | B | Ta | Hf | Other | ||||
| III-2O/III-46 | 0.25 | 0.41 | 0.44 | 0.021 | 0.018 | 0.0166 | 0.0008 | 0.0016 | 0.0008 | 0.0008 | 0.0008 | 0.00008 | 0.00006 | 0.00006 | - | 0.0152 | 0.0014 | III-f |
| III-2P/III-47 | 0.33 | 0.15 | 0.64 | 0.038 | 0.029 | 0.0142 | 0.0009 | 0.0016 | 0.0008 | 0.0008 | 0.0009 | 0.00008 | 0.00006 | 0.00006 | - | 0.0127 | 0.0015 | III-i |
| III-2Q/III-48 | 0.06 | 0.15 | 0.11 | 0.016 | 0.008 | 0.0299 | 0.0009 | 0.0017 | 0.0008 | 0.0009 | 0.0008 | 0.00007 | 0.00007 | 0.00005 | - | 0.0284 | 0.0016 | III-h |
| III-2R/III-49 | 0.34 | 0.34 | 0.87 | 0.024 | 0.004 | 0.0219 | 0.0009 | 0.0017 | 0.0008 | 0.0008 | 0.0008 | 0.00007 | 0.00007 | 0.00006 | - | 0.0204 | 0.0015 | III-f |
| III-2S/III-50 | 0.21 | 0.34 | 1.08 | 0.012 | 0.006 | 0.0089 | 0.0045 | 0.0015 | 0.0008 | 0.0008 | 0.0007 | 0.00008 | 0.00007 | 0.00005 | - | 0.0056 | 0.0033 | III-j |
| III-2T/III-51 | 0.31 | 0.29 | 0.10 | 0.025 | 0.011 | 0.0167 | 0.0009 | 0.0017 | 0.0008 | 0.0008 | 0.0008 | 0.00008 | 0.00006 | 0.00006 | - | 0.0152 | 0.0015 | III-g |
| III-2U/III-52 | 0.35 | 0.04 | 0.84 | 0.023 | 0.034 | 0.0102 | 0.0017 | 0.0017 | 0.0009 | 0.0008 | 0.0008 | 0.00200 | 0.00006 | 0.00006 | - | 0.0057 | 0.0045 | III-c |
| III-2V/III-53 | 0.08 | 0.54 | 0.43 | 0.008 | 0.012 | 0.0123 | 0.0008 | 0.0230 | 0.0008 | 0.0007 | 0.0008 | 0.00009 | 0.00006 | 0.00006 | - | 0.0046 | 0.0077 | III-e |
| III-2W/III-54 | 0.11 | 0.40 | 0.08 | 0.032 | 0.019 | 0.0067 | 0.0008 | 0.0017 | 0.0008 | 0.0034 | 0.0008 | 0.00008 | 0.00007 | 0.00007 | - | 0.0045 | 0.0022 | III-h |
| III-2X/III-55 | 0.15 | 0.31 | 0.21 | 0.021 | 0.019 | 0.0248 | 0.0008 | 0.0016 | 0.0008 | 0.0007 | 0.0008 | 0.00008 | 0.00006 | 0.00007 | - | 0.0234 | 0.0014 | III-f |
| III-2Y/III-56 | 0.38 | 0.41 | 1.56 | 0.020 | 0.010 | 0.0148 | 0.0008 | 0.0016 | 0.0008 | 0.0006 | 0.0007 | 0.00007 | 0.00006 | 0.00007 | - | 0.0135 | 0.0014 | III-g |
| III-2Z/III-57 | 0.51 | 0.11 | 1.54 | 0.041 | 0.005 | 0.0091 | 0.0021 | 0.0025 | 0.0007 | 0.0033 | 0.0006 | 0.00018 | 0.00006 | 0.00007 | - | 0.0059 | 0.0032 | III-b |
| III-3A/III-58 | 0.28 | 0.47 | 0.35 | 0.013 | 0.014 | 0.0162 | 0.0007 | 0.0017 | 0.0007 | 0.0007 | 0.0007 | 0.00008 | 0.00006 | 0.00006 | Co：4.2 | 0.0148 | 0.0014 | III-d |
| III-3B/III-59 | 0.34 | 0.23 | 0.44 | 0.004 | 0.044 | 0.0188 | 0.0007 | 0.0016 | 0.0008 | 0.0007 | 0.0007 | 0.00008 | 0.00006 | 0.00005 | Mo：0.08，Pb：0.02 | 0.0174 | 0.0014 | III-c |
| III-3C/III-60 | 0.25 | 0.05 | 0.12 | 0.011 | 0.018 | 0.0154 | 0.0008 | 0.0016 | 0.0008 | 0.0008 | 0.0008 | 0.00008 | 0.00006 | 0.00005 | Mo：1.5 | 0.0139 | 0.0014 | III-e |
| III-3D/III-61 | 0.13 | 0.13 | 0.70 | 0.017 | 0.005 | 0.0137 | 0.0008 | 0.0016 | 0.0008 | 0.0009 | 0.0008 | 0.00008 | 0.00007 | 0.00005 | W：1.2 | 0.0122 | 0.0015 | III-b |
| III-3E/III-62 | 0.26 | 0.12 | 1.02 | 0.012 | 0.026 | 0.0201 | 0.0008 | 0.0017 | 0.0009 | 0.0009 | 0.0009 | 0.00007 | 0.00007 | 0.00005 | W：0.08，Ca：0.024 | 0.0185 | 0.0015 | III-e |
| III-3F/III-63 | 0.05 | 0.15 | 0.17 | 0.001 | 0.017 | 0.0252 | 0.0008 | 0.0015 | 0.0009 | 0.0009 | 0.0008 | 0.00006 | 0.00007 | 0.00006 | Ca：0.011 | 0.0238 | 0.0014 | III-h |
| III-3G/III-64 | 0.31 | 0.13 | 1.23 | 0.038 | 0.043 | 0.0258 | 0.0007 | 0.0016 | 0.0008 | 0.0009 | 0.0008 | 0.00007 | 0.00007 | 0.00006 | Ca：0.04，REM：0.01 | 0.0244 | 0.0014 | III-f |
| III-3H/III-65 | 0.40 | 0.12 | 0.60 | 0.032 | 0.015 | 0.0125 | 0.0007 | 0.0016 | 0.0008 | 0.0009 | 0.0008 | 0.00007 | 0.00007 | 0.00007 | REM：0.03 | 0.0111 | 0.0014 | III-d |
| III-3I/III-66 | 0.38 | 0.12 | 0.46 | 0.021 | 0.034 | 0.0168 | 0.0006 | 0.0015 | 0.0008 | 0.0008 | 0.0008 | 0.00008 | 0.00006 | 0.00007 | Mg：0.015，Cr：1.7 | 0.0155 | 0.0013 | III-j |
| III-3J/III-67 | 0.15 | 0.22 | 0.40 | 0.012 | 0.009 | 0.0114 | 0.0006 | 0.0015 | 0.0008 | 0.0008 | 0.0008 | 0.00008 | 0.00006 | 0.00008 | Li：0.012 | 0.0101 | 0.0013 | III-b |
| III-3K/III-68 | 0.31 | 0.42 | 0.31 | 0.035 | 0.018 | 0.0141 | 0.0006 | 0.0015 | 0.0008 | 0.0008 | 0.0006 | 0.00009 | 0.00006 | 0.00008 | Mg：0.011，Ca：0.02 | 0.0128 | 0.0013 | III-i |
| III-3L/III-69 | 0.37 | 0.44 | 0.12 | 0.009 | 0.027 | 0.0165 | 0.0007 | 0.0014 | 0.0008 | 0.0008 | 0.0006 | 0.00008 | 0.00006 | 0.00008 | Co：3.4，Mo：0.8 | 0.0152 | 0.0013 | III-f |
| III-3M/III-70 | 0.27 | 0.17 | 0.15 | 0.008 | 0.005 | 0.0240 | 0.0007 | 0.0014 | 0.0008 | 0.0008 | 0.0006 | 0.00008 | 0.00007 | 0.00007 | Cu：0.5 | 0.0227 | 0.0013 | III-e |
| III-3N/III-71 | 0.25 | 0.26 | 0.34 | 0.007 | 0.011 | 0.0157 | 0.0008 | 0.0014 | 0.0008 | 0.0008 | 0.0006 | 0.00008 | 0.00006 | 0.00007 | Cu：2.1，Cr：1.2 | 0.0144 | 0.0014 | III-e |
| III-3O/III-72 | 0.34 | 0.32 | 0.29 | 0.036 | 0.020 | 0.0147 | 0.0006 | 0.0014 | 0.0007 | 0.0008 | 0.0006 | 0.00008 | 0.00006 | 0.00006 | Cu：0.9，Ni：2.1 | 0.0135 | 0.0012 | III-g |
| III-3P/III-73 | 0.42 | 0.34 | 0.73 | 0.044 | 0.010 | 0.0234 | 0.0007 | 0.0006 | 0.0007 | 0.0008 | 0.0008 | 0.00008 | 0.00006 | 0.00006 | Ni：2.4，Bi：0.05 | 0.0223 | 0.0011 | III-e |
| III-3Q/III-74 | 0.33 | 0.13 | 1.90 | 0.003 | 0.011 | 0.0150 | 0.0006 | 0.0015 | 0.0008 | 0.0009 | 0.0008 | 0.00006 | 0.00006 | 0.00006 | Ni：1.2 | 0.0137 | 0.0013 | III-b |
| III-3R/III-75 | 0.25 | 0.20 | 0.25 | 0.021 | 0.005 | 0.0128 | 0.0006 | 0.0015 | 0.0007 | 0.0009 | 0.0008 | 0.00006 | 0.00005 | 0.00006 | Co：0.8，Pb：0.03 | 0.0115 | 0.0013 | III-c |
| III-3S/III-76 | 0.27 | 0.08 | 0.28 | 0.039 | 0.012 | 0.0092 | 0.0006 | 0.0015 | 0.0008 | 0.0009 | 0.0007 | 0.00006 | 0.00005 | 0.00007 | Mo：1.5 | 0.0079 | 0.0013 | III-a |
[table 17]
| Heat treatment mode | Heating temperature (℃) | Hot-work | Speed of cooling (℃/s) | The cooling stop temperature (℃) |
| III-a | 800 | Have | 1 | 300 |
| III-b | 800 | Do not have | 1 | 400 |
| III-c | 900 | Have | 1 | 500 |
| III-d | 900 | Do not have | 1 | 300 |
| III-e | 1000 | Have | 0.5 | 300 |
| III-f | 1000 | Have | 1 | 500 |
| III-g | 1000 | Do not have | 5 | 400 |
| III-h | 1000 | Have | 10 | 500 |
| III-i | 1100 | Have | 1 | 300 |
| III-j | 1200 | Have | 1 | 500 |
Then, processing rate of straining: 0.001～240/s, processing temperature: 20～400 ℃, rate of compression: under 20～80% the processing conditions, processing thermal analogy (formaster) testing apparatus of use capacity 200kN forges table 15 and the described test film of table 16, and is processed into part.Rate of straining adopts the rate of straining mean value of (in the viscous deformation) in the processing.
For the part that obtains, adopt stereomicroscope, observe the surface with 20 times observation multiplying powers, confirm to have flawless.The processing conditions of each part, there are flawless and resistance to deformation to be presented in table 18 and the table 19.
Diameter of part) and measure number of times in addition, at load: 1000g, locate: the D/4 central part in test film cross section (D:: under 5 times the condition, use Vickers microhardness trier, measure the Vickers' hardness (Hv) of part.The hardness of each part (Hv) is presented in table 18 and the table 19.
[table 18]
| Part No. | The steel mark | Rate of straining (/s) | Processing temperature (℃) | Rate of compression (%) | Resistance to deformation (MPa) | Processing back part hardness (Hv) | (3) whether formula is set up | Flawless is arranged |
| III-1 | III-1A | 100 | 60 | 20 | 365 | 237 | ○ | Have |
| III-2 | III-1B | 140 | 80 | 80 | 417 | 254 | ○ | Do not have |
| III-3 | III-1C | 180 | 20 | 60 | 428 | 243 | ○ | Do not have |
| III-4 | III-1D | 220 | 60 | 80 | 486 | 261 | ○ | Do not have |
| III-5 | III-1E | 120 | 20 | 40 | 706 | 302 | ○ | Do not have |
| III-6 | III-1F | 100 | 40 | 80 | 785 | 313 | ○ | Have |
| III-7 | III-1G | 160 | 60 | 80 | 448 | 261 | ○ | Have |
| III-8 | III-1H | 140 | 20 | 60 | 515 | 272 | ○ | Do not have |
| III-9 | III-1I | 100 | 80 | 60 | 461 | 251 | ○ | Do not have |
| III-10 | III-1J | 180 | 20 | 80 | 548 | 273 | ○ | Do not have |
| III-11 | III-1K | 140 | 100 | 80 | 528 | 270 | ○ | Do not have |
| III-12 | III-1L | 220 | 20 | 20 | 559 | 284 | ○ | Do not have |
| III-13 | III-1M | 160 | 60 | 80 | 454 | 263 | ○ | Do not have |
| III-14 | III-1N | 100 | 40 | 40 | 513 | 259 | ○ | Have |
| III-15 | III-1O | 120 | 20 | 60 | 426 | 266 | ○ | Have |
| III-16 | III-1P | 240 | 60 | 80 | 474 | 255 | ○ | Do not have |
| III-17 | III-1Q | 200 | 80 | 20 | 509 | 258 | ○ | Do not have |
| III-18 | III-1R | 140 | 20 | 80 | 611 | 318 | ○ | Do not have |
| III-19 | III-1S | 180 | 20 | 20 | 483 | 295 | ○ | Do not have |
| III-20 | III-1T | 140 | 20 | 80 | 579 | 294 | ○ | Do not have |
| III-21 | III-1U | 100 | 20 | 20 | 531 | 276 | ○ | Do not have |
| III-22 | III-1V | 160 | 40 | 60 | 725 | 329 | ○ | Do not have |
| III-23 | III-1W | 220 | 20 | 40 | 693 | 295 | ○ | Do not have |
| III-24 | III-1X | 120 | 60 | 80 | 769 | 317 | ○ | Have |
| III-25 | III-1Y | 100 | 20 | 80 | 586 | 284 | ○ | Have |
| III-26 | III-1Z | 140 | 80 | 80 | 543 | 301 | ○ | Have |
| III-27 | III-2A | 200 | 20 | 20 | 555 | 269 | ○ | Have |
| III-28 | III-2B | 100 | 40 | 80 | 538 | 260 | ○ | Have |
| III-29 | III-2C | 160 | 20 | 20 | 537 | 251 | × | Do not have |
| III-30 | III-2D | 180 | 20 | 60 | 619 | 272 | ○ | Do not have |
| III-31 | III-2E | 0.001 | 20 | 80 | 671 | 298 | ○ | Have |
| III-32 | ″ | 0.1 | 60 | 80 | 601 | 291 | ○ | Have |
| III-33 | ″ | 1 | 20 | 40 | 566 | 295 | ○ | Have |
| III-34 | ″ | 10 | 80 | 80 | 531 | 284 | ○ | Have |
| III-35 | ″ | 100 | 100 | 20 | 496 | 302 | ○ | Do not have |
| III-36 | ″ | 200 | 200 | 60 | 486 | 307 | ○ | Do not have |
| III-37 | III-2F | 220 | 300 | 80 | 548 | 360 | ○ | Have |
| III-38 | III-2G | 140 | 400 | 20 | 662 | 304 | ○ | Have |
| III-39 | III-2H | 100 | 20 | 80 | 602 | 311 | ○ | Do not have |
| III-40 | III-2I | 160 | 20 | 80 | 479 | 273 | ○ | Do not have |
[table 19]
| Part No. | The steel mark | Rate of straining (/s) | Processing temperature (℃) | Rate of compression (%) | Resistance to deformation (MPa) | Processing back part hardness (Hv) | (2) whether formula is set up | Flawless is arranged |
| III-41 | III-2J | 120 | 60 | 40 | 463 | 271 | ○ | Do not have |
| III-42 | III-2K | 180 | 80 | 60 | 629 | 292 | ○ | Have |
| III-43 | III-2L | 100 | 80 | 20 | 607 | 335 | ○ | Do not have |
| III-44 | III-2M | 140 | 20 | 80 | 593 | 309 | ○ | Do not have |
| III-45 | III-2N | 220 | 20 | 80 | 568 | 279 | ○ | Do not have |
| III-46 | III-2O | 120 | 60 | 20 | 548 | 286 | ○ | Do not have |
| III-47 | III-2P | 200 | 40 | 80 | 567 | 310 | ○ | Do not have |
| III-48 | III-2Q | 160 | 100 | 40 | 433 | 273 | ○ | Do not have |
| III-49 | III-2R | 100 | 20 | 20 | 548 | 322 | ○ | Do not have |
| III-50 | III-2S | 180 | 40 | 80 | 691 | 261 | × | Do not have |
| III-51 | III-2T | 100 | 20 | 60 | 537 | 279 | ○ | Do not have |
| III-52 | III-2U | 140 | 60 | 80 | 771 | 274 | × | Do not have |
| III-53 | III-2V | 200 | 20 | 40 | 470 | 234 | × | Do not have |
| III-54 | III-2W | 160 | 80 | 20 | 466 | 223 | × | Do not have |
| III-55 | III-2X | 220 | 20 | 40 | 498 | 273 | ○ | Do not have |
| III-56 | III-2Y | 180 | 150 | 80 | 687 | 300 | ○ | Do not have |
| III-57 | III-2Z | 100 | 20 | 40 | 985 | 317 | × | Do not have |
| III-58 | III-3A | 120 | 40 | 60 | 560 | 313 | ○ | Do not have |
| III-59 | III-3B | 100 | 60 | 80 | 626 | 326 | ○ | Do not have |
| III-60 | III-3C | 160 | 20 | 80 | 524 | 269 | ○ | Do not have |
| III-61 | III-3D | 140 | 80 | 60 | 470 | 273 | ○ | Do not have |
| III-62 | III-3E | 200 | 20 | 80 | 590 | 277 | ○ | Do not have |
| III-63 | III-3F | 220 | 20 | 80 | 410 | 255 | ○ | Do not have |
| III-64 | III-3G | 100 | 150 | 20 | 585 | 292 | ○ | Do not have |
| III-65 | III-3H | 100 | 40 | 60 | 579 | 313 | ○ | Do not have |
| III-66 | III-3I | 180 | 60 | 40 | 575 | 288 | ○ | Do not have |
| III-67 | III-3J | 200 | 80 | 80 | 469 | 267 | ○ | Do not have |
| III-68 | III-3K | 100 | 20 | 40 | 568 | 310 | ○ | Do not have |
| III-69 | III-3L | 120 | 20 | 60 | 636 | 296 | ○ | Do not have |
| III-70 | III-3M | 180 | 20 | 80 | 571 | 278 | ○ | Do not have |
| III-71 | III-3N | 240 | 60 | 20 | 534 | 261 | ○ | Do not have |
| III-72 | III-3O | 140 | 20 | 60 | 605 | 295 | ○ | Do not have |
| III-73 | III-3P | 160 | 40 | 80 | 680 | 327 | ○ | Do not have |
| III-74 | III-3Q | 220 | 40 | 40 | 617 | 297 | ○ | Do not have |
| III-75 | III-3R | 100 | 60 | 60 | 528 | 259 | ○ | Do not have |
| III-76 | III-3S | 160 | 20 | 80 | 589 | 275 | ○ | Do not have |
In the present embodiment, part does not have crackle, and the steel low with respect to the resistance to deformation of part hardness steel (being to satisfy following formula (3) specifically) is judged to be the cold-workability excellence.Also have, as part strength, recommending Vickers' hardness is more than 240 (Hv).
Also have, in table 18 and table 19, show also whether each test film satisfies following formula (3), is designated as " zero " when satisfying formula (3), is designated as when not satisfying formula (3) " * ".
Result according to table 18 and table 19 can carry out following investigation.
Part No.III-2～III-5 (Steel Mark III-1B～III-1E), part No.III-8～III-13 (Steel Mark III-1H～III-1M), part No.III-30 (Steel Mark III-2D), part No.III-35～III-36 (Steel Mark III-2E), part No.III-39～III-41 (Steel Mark III-2H～III-2J), part No.III-43～III-49 (Steel Mark III-2L～III-2R), part No.III-51 (Steel Mark III-2T), part No.III-55～III-56 (Steel Mark III-2X～III-2Y), (Steel Mark III-3A～III-3S) all is the steel grades that adopt the regulation that satisfies the 3rd embodiment of the present invention to part No.III-58～III-76, implements the cold worked example of high speed with the method that the present invention recommends.The balance of its cold-workability of high-speed cold working part (wire rod/bar steel) shown in the above-mentioned part No. and intensity (hardness) and anti-crackle are all excellent.
With respect to this, the following example of specific important document in the 3rd embodiment of discontented unabridged version invention as explanation respectively, has crackle to take place being carried out on the cold worked part of high speed, or the balanced differences of cold-workability and intensity (hardness) (not satisfying following formula (3)).
Part No.III-1 has been to use the example of the few Steel Mark III-1A of C amount, and crackle has taken place after the processing.
Part No.III-6 has been to use the example of the many Steel Mark III-1F of C amount, because the scope of C overshoot, so crackle takes place.
Part No.III-7 has been to use the example of the few Steel Mark III-1G of Si amount, because Si lacks than the scope of regulation, so crackle takes place.
Part No.III-14 is to use the example of the many Steel Mark III-1N of Si amount, because the Si amount surpasses the scope of regulation, crackle takes place.
Part No.III-15 has been to use the example of the few Steel Mark III-10 of Mn amount, because Mn lacks than the scope of regulation, so crackle takes place.
Part No.III-24 has been to use the example of the many Steel Mark III-1X of Mn amount, because Mn surpasses the scope of regulation, so crackle takes place.
Part No.III-25 and part No.III-26 have been to use the many Steel Mark III-1Y of P amount that the example of III1Z is arranged, because the P amount surpasses the scope of regulation, crackle take place.
Part No.III-27 and No.III-28 have been to use many Steel Mark III-2A of S amount and the example of III2B, because S surpasses the scope of regulation, so crackle takes place.
Part No.III-29 has been to use the example of the few Steel Mark III-2C of N amount, because N lacks than the scope of regulation, solid solution N amount is few, so the balanced differences of cold-workability and hardness.
Part No.III-42 has been to use the example of the many Steel Mark III-2K of N amount, because N surpasses the scope of regulation, so crackle takes place.
Though part No.III-31～No.III-34 adopts the steel of the Steel Mark III-2E that the one-tenth of the regulation that satisfies the 3rd embodiment of the present invention is grouped into, it is slow that high speed cold adds the rate of straining in man-hour, and dynamic strain aging takes place, and cracks.
Part No.III-37～No.III-38, though adopt the steel of Steel Mark III-2F～III-2G that the one-tenth of the regulation satisfy the 3rd embodiment of the present invention is grouped into, high speed cold adds the temperature height in man-hour, dynamic strain aging takes place, and cracks.
Part No.III-50 has been to use the Al amount many, does not satisfy the example of the Steel Mark III-2S of formula (2), the balanced differences of cold-workability and hardness.
It is many that part No.III-52 has been to use Al amount, B to measure, and do not satisfy the example of the Steel Mark III-2U of formula (2), the balanced differences of cold-workability and hardness.
Part No.III-53 has been to use the Ti amount many, does not satisfy the example of the Steel Mark III-2V of formula (2), the balanced differences of cold-workability and hardness.
Part No.III-54 has been to use the V amount many, does not satisfy the example of the Steel Mark III-2W of formula (2), the balanced differences of cold-workability and hardness.
It is all many respectively that part No.III-57 has been to use Ti amount, V amount, B to measure, and do not satisfy the example of the Steel Mark III-2Z of formula (2), the balanced differences of cold-workability and hardness.
Claims (15)
1. steel for high-speed cold working is characterized in that % contains in quality:
C：0.03％～0.6％、
Si：0.005～0.6％、
Mn：0.05～2％、
P:0.05% following but do not contain 0%,
S:0.05% following but do not contain 0%,
N:0.04% is following but do not contain 0%,
Surplus is iron and unavoidable impurities,
Solid solution nitrogen amount in the steel is more than 0.006%.
2. steel for high-speed cold working according to claim 1 is characterized in that C content counts 0.03～0.15% with quality %.
3. steel for high-speed cold working according to claim 1 is characterized in that, C content counts 0.15～0.6% and do not contain 0.15% with quality %.
4. steel for high-speed cold working according to claim 1 is characterized in that % contains more than the N:0.007% in quality.
5. steel for high-speed cold working according to claim 1 is characterized in that, also contains below the Al:0.1% in quality % but does not contain 0%.
6. steel for high-speed cold working according to claim 1 is characterized in that, also contains at least a kind that selects from following element in quality %:
Zr:0.2% following but do not contain 0%,
Ti:0.1% following but do not contain 0%,
Nb:0.1% following but do not contain 0%,
V:0.5% following but do not contain 0%,
Ta:0.1% following but do not contain 0%,
Hf:0.1% is following but do not contain 0%.
7. steel for high-speed cold working according to claim 1 is characterized in that, also contains below the B:0.0015% in quality % but does not contain 0% and/or below the Cr:2% but do not contain 0%.
8. steel for high-speed cold working according to claim 1 is characterized in that, satisfies following formula (1),
[N]-(14[Al]/27+14[Ti]/47.9+14[Nb]/92.9+14[V]/50.9+14[Zr]/91.2+14[B]/10.8+14[Ta]/180.9+14[Hf]/178.5) 〉=0.006 ... (1) formula
In the formula (1), [] represents the total mass degree of each element in steel.
9. steel for high-speed cold working according to claim 1 is characterized in that, the content of described unavoidable impurities is satisfied in quality %:
Al:0.001% is following and contain 0%,
Ti:0.002% is following and contain 0%,
Nb:0.001% is following and contain 0%,
V:0.001% is following and contain 0%,
Zr:0.001% is following and contain 0%,
B:0.0001% is following and contain 0%,
Ta:0.0001% is following and contain 0%,
Hf:0.0001% is following and contain 0%,
And, satisfy following formula (2),
14[Al]/27+14[Ti]/47.9+14[Nb]/92.9+14[V]/50.9+14[Zr]/91.2+14[B]/10.8+14[Ta]/180.9+14[Hf]/178.5≤0.002% ... (2) formula
[] represents the total mass degree of each element in steel in formula (2).
10. steel for high-speed cold working according to claim 1, it is characterized in that, also contain at least a kind that selects from following element, the content of this element is counted with quality %, and: Cr:2% is following but do not contain 0%, Cu:5% is following but do not contain 0%, Ni:5% is following but do not contain 0%, Co:5% is following but do not contain 0%, Mo:2% is following but do not contain 0%, W:2% is following but do not contain 0%, Ca:0.05% is following but do not contain 0%, rare earth element: below 0.05% but do not contain 0%, Mg:0.02% is following but do not contain 0%, Li:0.02% is following but do not contain 0%, Pb:0.1% is following but do not contain 0%, Bi:0.1% is following but do not contain 0%.
11. the manufacture method of a high-speed cold working part is characterized in that, with the processing temperature below 200 ℃ each described steel for high-speed cold working in the claim 1～10 is carried out high speed cold processing.
12. the manufacture method of a high-speed cold working part is characterized in that, is under the condition more than the 100/s each described steel for high-speed cold working in the claim 1～10 to be carried out high speed cold processing at rate of straining.
13. the manufacture method of a steel for high-speed cold working is characterized in that, will have the steel that each described one-tenth is grouped in the claim 1～8, is heated to Ac
3Temperature more than point+30 ℃ is at Ac
3After temperature province more than point+30 ℃ was carried out hot-work, the speed of cooling above with 0.5 ℃/s was cooled to below 500 ℃.
14. the manufacture method of a steel for high-speed cold working is characterized in that, will have the steel that each described one-tenth is grouped in the claim 1～8, is heated to Ac
3After the temperature more than point+30 ℃, the speed of cooling above with 0.5 ℃/s is cooled to below 500 ℃.
15. high-speed cold working part, it is characterized in that, be under the processing temperature below 200 ℃, the condition of rate of straining more than the 100/s, each described steel for high-speed cold working in the claim 1～10 is carried out the high speed cold processing and manufacturing to form, wherein, part strength H after the high speed cold processing, and high speed cold processing in the maximum value DR of resistance to deformation satisfy following formula (3)
H 〉=(DR+1000)/6 ... (3) formula
Wherein, H: part strength (Hv), DR: resistance to deformation (MPa).
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| JP2006355497 | 2006-12-28 | ||
| JP2006355497A JP4295314B2 (en) | 2006-12-28 | 2006-12-28 | Steel for high-speed cold work, method for producing the same, and method for producing high-speed cold-worked parts |
| JP2007097457 | 2007-04-03 | ||
| JP2007103027 | 2007-04-10 |
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| JP2008163410A (en) | 2008-07-17 |
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