CN101410541B - Steel for machine structure excelling in machinability and strength property - Google Patents

Steel for machine structure excelling in machinability and strength property Download PDF

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CN101410541B
CN101410541B CN2007800109591A CN200780010959A CN101410541B CN 101410541 B CN101410541 B CN 101410541B CN 2007800109591 A CN2007800109591 A CN 2007800109591A CN 200780010959 A CN200780010959 A CN 200780010959A CN 101410541 B CN101410541 B CN 101410541B
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steel
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machinability
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CN101410541A (en
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宫西庆
桥村雅之
水野淳
宫本健一郎
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Nippon Steel Corp
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C21D1/28—Normalising
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/02—Hardening by precipitation
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite

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  • Crystallography & Structural Chemistry (AREA)
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  • Heat Treatment Of Steel (AREA)

Abstract

A steel for machine structure that in a wide range of cutting speed, exhibits appropriate machinability, and that simultaneously has high impact performance and high yield ratio. The steel for machine structure is one excelling in machinability and strength property, comprising, by mass, 0.1 to 0.85% C, 0.01 to 1.5% Si, 0.05 to 2.0% Mn, 0.005 to 0.2% P, 0.001 to 0.15% S, over 0.05 to 0.3% total Al, less than 0.0150% Sb (including 0%), 0.0035 to 0.020% total N wherein solid solution N is limited to 0.0020% or less, and the balance Fe and unavoidable impurities.

Description

The steel for mechanical structure of machinability and strength characteristics excellence
Technical field
The present invention relates to implement the steel for mechanical structure of machining, relate in particular to and can be used for the machinability (machinability in more wide in range cutting speed district to the machining in the higher speed districts such as vertical turning of hard alloy coating instrument than the machining of low regime from High Speed Steel Bit; Machinability) and the steel for mechanical structure of strength characteristics excellence.
Background technology
In recent years, the high strength of steel is constantly progressive, but produces the problem that workability reduces thereupon.Therefore, to keeping intensity and not making the upswing in demand of the steel that stock-removing efficiency reduces.Past people knows that the machinability in order to make steel improves, and the element that adds raising machinabilitys such as S, Pb and Bi is effective.Yet people are known, and are also less to forged influence though Pb improves machinability with regard to Bi, and strength characteristics is reduced.
In addition, recently, Pb becomes environmental pressure and exists and avoid the tendency used, and its usage quantity is the trend of reduction.In addition, what S formed MnS and so on becomes soft inclusion at the cutting environment, and machinability is improved, but the size of MnS is bigger than the particle of Pb etc., becomes stress raiser easily.Particularly when by forging and rolling the extension, owing to MnS produces anisotropy, the specific direction of steel dies down terrifically.In addition, on the design steel, must consider such anisotropy.Therefore, under the situation of adding S, it is essential that the technology that makes anisotropy hang down limitization becomes.
As mentioned above, even add improving the machinability effective elements, its strength characteristics also reduces, and therefore is difficult to have both strength characteristics and machinability.Therefore, have both machinability and strength characteristics in order to make steel, further technical renovation is necessary.
So; a kind of steel for mechanical structure was once proposed in the past; its contain add up to 0.005 quality % above be selected from more than one of for example solid solution V, solid solution Nb and solid solution Al; and contain the solid solution N more than 0.001%; in cutting, make the nitride that generates owing to heat in metal cutting attached on the instrument thus; play the function of instrument protective membrane, thereby can prolong the cutting tool life-span in (with reference to TOHKEMY 2004-107787 communique).In addition, a kind of steel for mechanical structure was also once proposed, in the content of regulation C, Si, Mn, S and Mg, the ratio of regulation Mg content and S content, and aspect ratio and number optimizing by making the sulfide-based inclusion in the steel, seek to improve smear metal property handled and mechanical characteristics (with reference to No. 3706560 communique of Japanese Patent).No. 3706560 described steel for mechanical structure of communique of this Japanese Patent, Mg is controlled at (do not comprise 0%) below 0.02% in, also its content is limited to below 0.1% containing under the situation of Al.
Summary of the invention
But there is the problem of the following stated in above-mentioned prior art.Promptly can infer, the described steel of TOHKEMY 2004-107787 communique, if by the caused thermal value of cutting when to a certain degree above, just can not cause above-mentioned phenomenon.Therefore, be limited in the high speed cutting of the degree of the cutting speed with performance effect, existence can not expect to obtain the problem of the effect under low regime.In addition, No. 3706560 described steel of communique of Japanese Patent shows no sign of consideration about strength characteristics.And No. 3706560 described steel of communique of Japanese Patent also shows no sign of consideration about cutting tool life-span and yield ratio, therefore has the problem that can not obtain the full intensity characteristic.
The present invention is in view of the above-mentioned problems and proposes that its purpose is, is provided at wide in range cutting speed zone and has good machinability, and have the steel for mechanical structure of high impact characteristics and high yield ratio simultaneously.
The steel for mechanical structure of machinability of the present invention and strength characteristics excellence, it is characterized in that, in quality %, contain C:0.1～0.85%, Si:0.01～1.5%, Mn:0.05～2.0%, P:0.005～0.2%, S:0.001～0.15%, whole Al: surpass 0.05% and be 0.3% below, Sb: be lower than 0.0150% (comprising 0%) and whole N:0.0035～0.020%, and solid solution N is limited in below 0.0020%, and its surplus is made up of Fe and unavoidable impurities.
This steel for mechanical structure can also contain Ca:0.0003～0.0015 quality %.
In addition, in quality %, also can contain one or more the element that is selected among Ti:0.001～0.1%, Nb:0.005～0.2%, W:0.01～1.0% and V:0.01～1.0%.And then, in quality %, can contain one or more the element that is selected among Mg:0.0001～0.0040%, Zr:0.0003～0.01% and Rem:0.0001～0.015%.
And then, in quality %, can contain one or more the element that is selected among Sn:0.005～2.0%, Zn:0.0005～0.5%, B:0.0005～0.015%, Te:0.0003～0.2%, Bi:0.005～0.5% and Pb:0.005～0.5%.
And then, in quality %, can contain one or both elements that are selected among Cr:0.01～2.0% and Mo:0.01～1.0%.
And then, in quality %, can contain one or both elements that are selected among Ni:0.05～2.0% and Cu:0.01～2.0%.
Description of drawings
Fig. 1 is the figure that cut position of expression Charpy impact test with test piece.
Embodiment
Below be elaborated to implementing best mode of the present invention.The steel for mechanical structure of machinability of the present invention and strength characteristics excellence (the following steel for mechanical structure that also abbreviates as), in order to solve above-mentioned problem, one-tenth as steel is grouped into, in the addition of adjusting Al and other nitride generting element and N, by giving suitable thermal treatment, to suppress lowlyer to machinability and the deleterious solid solution N of impact characteristics, in addition, by guaranteeing an amount of solid solution Al that high-temperature embrittlement improves machinability that passes through, with Sb with matrix embrittlement effect, and guarantee that an amount of crystalline structure that passes through high-temperature embrittlement effect and divisibility makes the AlN of machinability raising, cutting speed district to from low speed to high speed wide region guarantees to have effective cutting ability, and, by improving the Al addition, compare with Al killed steel in the past, the segregation in strand stage is little, uniformly dispersed high MnS (according to the III type MnS of SIMS classification) increases, become the steel for mechanical structure that has high impact characteristics simultaneously, and be to separate out and solid solution Al by the fine of AlN, obtain the steel for mechanical structure of higher yield ratio.
Promptly, steel for mechanical structure of the present invention has following composition: in quality %, contain C:0.1～0.85%, Si:0.01～1.5%, Mn:0.05～2.0%, P:0.005～0.2%, S:0.0.15%, whole Al: surpass 0.05% and be 0.3% below, Sb: be lower than 0.0150% (comprising 0%) and whole N:0.0035～0.020%, and solid solution N is limited in below 0.0020%, and its surplus is made up of Fe and unavoidable impurities.
At first, each composition element and content thereof in the steel for mechanical structure of the present invention are described.In addition, in the following description, the quality % in the composition is designated as % simply.
C：0.1～0.85％
C is the element that the fundamental strength tool to steel has a significant impact.But, be lower than at 0.1% o'clock at C content, can not obtain full intensity, and other the alloying element of having to also drop in large quantities.And surpass at 0.85% o'clock at C content, and approach hypereutectoid, separate out the carbide of hard, so machinability reduces significantly morely.Therefore, in the present invention, in order to obtain full intensity, C content is defined as 0.1～0.85%, is limited to 0.2% under preferred.
Si：0.01～1.5％
Si is added as deoxidant element usually, but also has the effect that makes ferrite strengthen and give the temper softening drag.But, be lower than at 0.01% o'clock at Si content, can not obtain sufficient deoxidation effect.And surpass at 1.5% o'clock at Si content, embrittlement etc. takes place, and material behavior is descended, and also variation of machinability.Therefore, Si content is defined as 0.01～1.5%, is limited to 1.0% on preferred.
Mn：0.05～2.0％
Mn makes the sulphur (S) in the steel fix with the MnS form and disperse, and solid solution in matrix, be improve hardening capacity and guarantee to quench after the necessary element of intensity.But, being lower than at 0.05% o'clock at Mn content, the S in the steel combines with Fe and forms FeS, and steel becomes fragile.And Mn content is when increasing, and specifically, Mn content surpasses at 2.0% o'clock, and the hardness of matrix increases, and cold-workability reduces, and also saturated to the influence of intensity and hardening capacity.Therefore, Mn content is defined as 0.05～2.0%.
P：0.005～0.2％
P has the good effect of the machinability of making, but P content is lower than at 0.005 o'clock, can not obtain this effect.In addition, when P content increased, specifically, P content surpassed at 0.2% o'clock, and the hardness of matrix increases in the steel, and not only cold-workability reduces, and hot workability and forging characteristic also reduce.Therefore P content is defined as 0.005～0.2%.
S：0.001～0.15％
S combines with Mn with MnS inclusion form and exists.MnS has the effect that the machinability of making improves, and in order to obtain this effect significantly, needs to add the S more than 0.001%.On the other hand, descend significantly in the impact value of S content above 0.15% o'clock steel.Therefore under the situation of the raising of seeking machinability by interpolation S, S content is defined as 0.001～0.15%.
Whole Al: surpass 0.05% and be below 0.3%
Al also separates out whole granulation and the effective AlN of machinability except forming oxide compound, and becomes the effect that solid solution Al has the machinability of making raising.In order fully to generate, need to add 0.05% the amount that surpasses to the effective solid solution Al of this machinability.In addition, Al is to the crystallization of MnS with to separate out form also influential.Secondly, when add surpassing the Al of 0.05% amount, compare with Al killed steel in the past, the segregation in strand stage is less, and uniformly dispersed high MnS (according to the III type MnS of SIMS classification) is increased, therefore can be had the steel for mechanical structure of high impact characteristics simultaneously, and, separate out and solid solution Al by the fine of AlN, can obtain high yield ratio.But total Al content surpasses at 0.3% o'clock, and machinability begins to descend.Therefore total Al content is defined as above 0.05% and below 0.3%.Preferred total the following of Al content is limited to 0.08%, is limited to greater than 0.1% under further preferred.
Sb: be lower than for 0.0150% (comprising 0%)
Sb makes moderately embrittlement of ferrite, has the effect that the machinability of making improves.This effect is especially remarkable for a long time in solid solution Al amount, can't see this effect but Sb content is lower than at 0.0005% o'clock.On the other hand, when Sb content increased, specifically, Sb content was 0.0150% when above, and the macrosegregation of Sb is too much, and impact value reduces greatly.Therefore, Sb content is defined as more than 0.0005% and is lower than 0.0150%.Under the situation that does not need higher machinability or total Al content surpass under 0.1% the situation, can also not add (0%).
Whole N:0.0035～0.020%
N is except solid solution N, and also the nitride form with Ti, Al, V etc. exists, and suppresses the austenite crystal growth.But total N content is lower than at 0.0035% o'clock, can not get significant effect.On the other hand, total N content surpasses at 0.020% o'clock, becomes the reason of rolling defect in rolling process.Therefore, total N content is defined as 0.0035～0.020%.
Below the solid solution N:0.0020%
Solid solution N makes hardening of steel.Especially in cutting,, reduced life tools, in rolling, become the reason of rolling defect in addition because dynamic strain aging hardens near blade.Solid solution N measures for a long time, and specifically, solid solution N amount surpasses at 0.0020% o'clock, follows the increase of points hardness during cutting, and cutting resistance raises, and encourages tool wear thus.Therefore, solid solution N amount is suppressed at below 0.0020%.Thus can the friction of improvement instrument.In addition, solid solution N amount can cause the matrix embrittlement for a long time, and impact characteristics worsens, but if solid solution N amount is suppressed at below 0.0020%, can also improve this matrix embrittlement.Here said solid solution N amount, be to deduct the N that is contained the nitride such as AlN, NbN, TiN and VN from total N content to measure the value that obtains, for example, adopt rare gas element fusing-thermal conduction degree method to measure total N content, and the strainer of the SPEED method of the constant potential electrolytic etching method by adopting non-aqueous solvent electrolyte and the 0.1 μ m residue that carries out electrolytic extraction measures N content in the nitride by the indophenols absorbance method, thereby can be calculated by following formula (1).
Solid solution N amount=(total N content)-(N amount in the nitride) ... (1)
Moreover solid solution N amount can be suppressed lowlyer by method shown below.
1) in the scope of the present invention's regulation, suppress lowlyer total N content.The total N content scope dictates is below 0.020%, but preferably is suppressed at below 0.01%, further preferably is suppressed at below 0.006%.
2) under the high situation of total N content, add nitride generting element Al and other nitride generting element in right amount, the nitrogen compound amount is increased get final product.
3) reduce solid solution N for fine separating out, consider as steel for mechanical structure and use, from suppressing the viewpoint of thickization of crystal grain, preferred fine separating out by nitride.For fine the separating out by nitride reduced solid solution N amount, must keep the high temperature of complete solid solution according to N and nitride generting element amount, consider this point, carry out more than 1100 ℃, preferred more than 1200 ℃, more preferably after the solution heat treatment more than 1250 ℃, carry out thermal treatments such as normalizing and carburizing, it is separated out.Especially under the situation of AlN,, the amount of separating out is increased, reduce solid solution N by near 850 ℃, keeping long-time.At this, so-called long-time, be meant more than 0.8 hour, be preferably more than 1 hour, more preferably more than 1.2 hours.
In addition, in steel for mechanical structure of the present invention, except above-mentioned each composition, can also contain Ca.
Ca：0.0003～0.0015％
Ca is a deoxidant element, generates oxide compound in steel.Surpass 0.05% and be in the steel for mechanical structure of the present invention 0.3% below at total Al content, formation calcium aluminate (CaOAl 2O 3), this CaOAl 2O 3Be to compare Al 2O 3Low-melting oxide compound, therefore when high speed cutting, become the instrument protective membrane, have the effect that the machinability of making improves.But, be lower than at 0.0003% o'clock at Ca content, can not obtain this machinability and improve effect, and surpass at 0.0015% o'clock at Ca content, generate CaS in the steel, instead machinability reduces.Therefore, in the occasion of adding Ca, its content is defined as 0.0003～0.0015%.
In addition, in steel for mechanical structure of the present invention, make it form the occasion that carbonitride needs high strength, except above-mentioned each composition, can also contain one or more the element that is selected among Ti:0.001～0.1%, Nb:0.005～0.2%, W:0.01～1.0% and V:0.01～1.0%.
Ti：0.001～0.1％
Ti forms carbonitride, is to suppress the austenite crystal growth and to strengthening favourable element, at the steel that requires high strength and require in the low strained steel, can be used as and is used to prevent that the thick whole granulation element of crystal grain from using.In addition, Ti or deoxidant element form soft oxide compound by making it, also have the effect that the machinability of making improves.But, be lower than 0.001% occasion at Ti content, can't see its effect, and surpass at 0.1% o'clock at Ti content, can separate out the thick carbonitride of the not solid solution of the reason that becomes thermal crack, instead mechanical property suffers damage.Therefore, in the occasion of adding Ti, its content is defined as 0.001～0.1%.
Nb：0.005～0.2％
Nb also forms carbonitride; be by the secondary precipitation strength help steel reinforcement, suppress the austenite crystal growth and to strengthening favourable element; at the steel that requires high strength and require in the low strained steel, can be used as and be used to prevent that the thick whole granulation element of crystal grain from using.But, be lower than 0.005% occasion at Nb content, can not obtain the effect of high strength, and surpass at 0.2% o'clock at the Nb addition, can separate out the thick carbonitride of the not solid solution of the reason that becomes thermal crack, instead mechanical property suffers damage.Therefore, in the occasion of adding Nb, its content is defined as 0.005～0.2%.
W：0.01～1.0％
W also forms carbonitride, be to come element that steel is strengthened by the secondary precipitation strength, but, be lower than 0.01% occasion at W content, can not obtain the effect of high strength, and surpass at 1.0% o'clock at the W addition, and can separate out the thick carbonitride of the not solid solution of the reason that becomes thermal crack, instead mechanical property suffers damage.Therefore, in the occasion of adding W, its content is defined as 0.01～1.0%.
V：0.01～1.0％
V also forms carbonitride, is to come element that steel is strengthened by the secondary precipitation strength, can suitably add in requiring the steel of high strength.But, be lower than 0.01% occasion at V content, can not obtain the effect of high strength, and surpass at 1.0% o'clock at the V addition, can separate out the thick carbonitride of the not solid solution of the reason that becomes thermal crack, instead mechanical property suffers damage.Therefore, in the occasion of adding V, its content is defined as 0.05～1.0%.
In addition, in steel for mechanical structure of the present invention, carry out the occasion of oxide morphology control by the deoxidation adjustment, except above-mentioned each composition, can also add one or more the element that is selected among Mg:0.0001～0.0040%, Zr:0.0003～0.01% and Rem:0.0001～0.015%.
Mg：0.0001～0.0040％
Mg is a deoxidant element, generates oxide compound in steel.And be the occasion of prerequisite with the Al deoxidation, will be to the deleterious Al of machinability 2O 3Upgrading becomes more soft fine dispersive MgO or Al 2O 3MgO.In addition, its oxide compound becomes the nuclear of MnS easily, also has the fine dispersive effect of the MnS of making.But, be lower than at 0.0001% o'clock at Mg content, can't see its effect.Mg generates the complex sulfide with MnS in addition, and with the MnS nodularization, but when adding Mg, specifically, Mg content surpasses at 0.0040% o'clock, can promote independent MnS to generate, and makes the machinability variation superfluously.Therefore, in the occasion of adding Mg, its content is defined as 0.0001～0.0040%.
Zr：0.0003～0.01％
Zr is a deoxidant element, generates oxide compound in steel.Its oxide compound can be thought ZrO 2, because this ZrO 2Become the nuclear of separating out of MnS, the site of separating out of MnS is increased, have the homodisperse effect of the MnS of making.In addition, Zr is solid-solubilized among the MnS, generates complex sulfide, and its energy of deformation is reduced, and also has the effect that the MnS shape is extended that suppresses when rolling and forge hot.Like this, Zr is to reducing the anisotropy effective elements.But, be lower than at 0.0003% o'clock at Zr content, can not obtain significant effect about these effects.On the other hand, the Zr addition surpasses at 0.01% o'clock, the extreme variation of qualification rate not only, and generate ZrO in a large number 2And the hard compounds of ZrS etc., instead mechanical properties such as machinability, impact value and fatigue characteristic reduce.Therefore, in the occasion of adding zr, its content is defined as 0.0003～0.01%.
Rem：0.0001～0.015％
Rem (rare earth element) is a deoxidant element, generate low melting point oxide, the obstruction of geat (nozzle) when not only suppressing casting, and solid solution or combination in MnS, its energy of deformation is reduced, when rolling and forge hot, also have the effect that the MnS shape is extended that suppresses.Therefore, Rem is to reducing the anisotropy effective elements.But, being lower than 0.0001% occasion in the total amount of Rem content, its effect is not remarkable.And surpass at 0.015% o'clock at the Rem addition, and generating the sulfide of Rem in a large number, machinability worsens.Therefore, in the occasion of adding Rem, its content is defined as 0.0001～0.015%.
In addition, in steel for mechanical structure of the present invention, in the occasion that machinability is improved, except above-mentioned each composition, can also add one or more the element that is selected among Sn:0.005～2.0%, Zn:0.0005～0.5%, B:0.0005～0.015%, Te:0.0003～0.2%, Bi:0.005～0.5% and Pb:0.005～0.5%.
Sn：0.005～2.0％
Sn makes the ferrite embrittlement, prolongs life tools, and has the effect that the surface smoothness of making improves.But Sn content is lower than at 0.005% o'clock, can't see its effect, and surpasses at 2.0% o'clock at the Sn addition, and its effect is saturated.Therefore, in the occasion of adding Sn, its content is defined as 0.005～2.0%.
Zn makes the ferrite embrittlement, prolongs life tools, and has the effect that the surface smoothness of making improves.But, be lower than 0.0005% occasion at Zn content, can't see its effect, and surpass at 0.5% o'clock at the Zn addition, its effect is saturated.Therefore, in the occasion of adding Zn, its content is defined as 0.0005～0.5%.
B：0.0005～0.015％
B is producing effect aspect grain-boundary strengthening and the hardening capacity under the situation of solid solution, under situation about separating out, owing to separate out with the BN form, therefore produces effect on machinability.It is not remarkable to be lower than 0.0005% o'clock these effect at B content.On the other hand, the B addition surpasses at 0.015% o'clock, and its effect is saturated, and BN separates out too much, so instead the mechanical property of steel suffers damage.Therefore, in the occasion of adding B, its content is defined as 0.0005～0.015%.
Te：0.0003～0.2％
Te improves the machinability element.In addition,, the energy of deformation of MnS is reduced, have the effect that the MnS shape is extended that suppresses by generating MnTe or coexisting with MnS.Therefore, Te is to reducing the favourable element of anisotropy.But, be lower than at 0.0003% o'clock at Te content, can't see these effects, and surpass at 0.2% o'clock at Te content, not only its effect is saturated, and the hot rolling reduction, becomes the reason of defective easily.Therefore, in the occasion of adding Te, its content is defined as 0.0003～0.2%.
Bi：0.005～0.5％
Bi is the element that improves machinability.But, be lower than at 0.005% o'clock at Bi content, can't see its effect, and surpass at 0.5% o'clock at the Bi addition, the effect that not only improves machinability is saturated, and the hot rolling reduction, becomes the reason of defective easily.Therefore, in the occasion of adding Bi, its content is defined as 0.005～0.5%.
Pb：0.005～0.5％
Pb is the element that improves machinability.But, be lower than 0.005% occasion at Pb content, can't see its effect, and the Pb addition surpasses at 0.5% o'clock, the effect that not only improves machinability is saturated, and the hot rolling reduction, becomes the reason of defective easily.Therefore, in the occasion of adding Pb, its content is defined as 0.005～0.5%.
In addition, in steel for mechanical structure of the present invention,, steel are given the occasion of intensity hardening capacity being improved and anti-temper softening being improved, except above-mentioned each composition, can also add in Cr:0.01～2.0% and Mo:0.05～1.0% one or both.
Cr：0.01～2.0％
Cr is an element of giving the temper softening drag when improving hardening capacity, can add in needing the steel of high strength.But Cr content is lower than 0.01% occasion, can't see these effects, and when heavy addition Cr, specifically, Cr content surpasses at 2.0% o'clock, can generate the carbide of Cr, makes the steel embrittlement.Therefore, in the occasion of adding Cr, its content is defined as 0.01～2.0%.
Mo：0.05～1.0％
Mo is the element that hardening capacity is improved, and can add in needing the steel of high strength.But Mo content is lower than 0.05% occasion and can't see these effects, and the Mo addition surpasses at 1.0% o'clock, and its effect is saturated.Therefore, in the occasion of adding Mo, its content is defined as 0.05～1.0%.
And then, in steel for mechanical structure of the present invention,, except above-mentioned each composition, can also add in Ni:0.05～2.0%, Cu:0.01～2.0% one or both in the occasion that ferrite is strengthened.
Ni：0.05～2.0％
Ni is when reinforced ferrite improves ductility, to improving hardening capacity and improving the solidity to corrosion effective elements.But, be lower than 0.05% occasion at Ni content, can't see its effect, and the Ni addition surpasses at 2.0% o'clock, consider that from the viewpoint of mechanical property effect is saturated, machinability reduces.Therefore, in the occasion of adding Ni, its content is defined as 0.05～2.0%.
Cu：0.01～2.0％
Cu is to improving hardening capacity and improving the solidity to corrosion effective elements in reinforced ferrite.But, be lower than 0.01% occasion at Cu content, can't see its effect, in addition,, consider that from the viewpoint of mechanical property its effect is also saturated even the Cu addition surpasses 2.0%.Therefore, in the occasion of adding Cu, its content is defined as 0.01～2.0%.Moreover Cu especially makes the hot rolling reduction, becomes the reason of the defective when rolling easily, and therefore preferred and Ni adds simultaneously.
As mentioned above, in steel for mechanical structure of the present invention,, therefore compare, machinability and impact characteristics are improved with steel for mechanical structure in the past owing to reduced solid solution N amount.In addition,, guarantee an amount of solid solution Al, Sb and AlN, therefore, can obtain effective cutting ability for the cutting speed district of from low speed to high speed wide region with the effect that improves machinability by making total Al content and Sb content optimizing.In addition, because this AlN fine separated out and the effect of solid solution Al, can obtain high yield ratio.In addition, owing to will influence suitableization of content of the element that MnS separates out, the amount of uniformly dispersed high MnS is increased, so also excellence of impact characteristics.
The steel for mechanical structure of machinability of the present invention and strength characteristics excellence, can carry out forge hot more than 1200 ℃ by the steel billet that will have above-mentioned steel composition, drawing-down become cylindrical after, carrying out solution heat treatment more than 1100 ℃, then carry out thermal treatments such as normalizing, carburizing and make.Especially for the steel that contains this mononitride of AlN, by keeping more than 0.8 hour after the solution heat treatment more than 1100 ℃, preferably keep more than 1 hour, more preferably keep long-time more than 1.2 hours, the steel for mechanical structure of the solid solution N that can be significantly reduced.
Embodiment 1
Then enumerating embodiment and comparative example specifies effect of the present invention.In the present embodiment, after the steel 150kg with the composition shown in vacuum melting furnace refining table 1 and the table 2, carry out forge hot under 1250 ℃ temperature condition, it is the cylindrical of 65mm that drawing-down becomes diameter.Then, each steel for this embodiment and comparative example carry out machinability test, Charpy impact test and tension test with following method, estimate its characteristic.Moreover the underscore in the table 2 is illustrated in outside the scope of the present invention.
Figure G2007800109591D00131
Figure G2007800109591D00141
Machinability test
Machinability test, at first for being heated to 1250 ℃ at the hot embodiment of drawing-down and each steel of comparative example of having carried out down, be implemented under 850 ℃ the temperature condition and carry out normalizing in 1 hour, wherein comparative example No.49, No.50 carry out normalizing in 0.5 hour, the thermal treatment of air cooling then.Then, each steel after thermal treatment cut machinability evaluation test piece, under the machining condition shown in the following table 3, carry out the bit bore test, and carry out vertical turning test, estimated the machinability of each steel of embodiment and comparative example in the condition shown in the following table 4.At this moment, as evaluation index, in the bit bore test, adopting machinable is the maximum cutting speed VL1000 of 1000mm to the accumulation hole depth, in vertically turning is tested, adopts the cutter back greatest wear width VB_max after 10 minutes.
Table 3
Figure G2007800109591D00151
Table 4
Charpy impact test
Fig. 1 is the figure that cut position of expression Charpy impact test with test piece.In Charpy impact test, at first as shown in Figure 1, from same method of above-mentioned machinability test and condition under carried out on heat treated each steel 1, cutting diameter is the cylinder material 2 of 25mm, and makes central shaft vertical with the drawing-down direction of steel 1.Then, for each cylinder material 2, carry out under 850 ℃ temperature condition, being incubated 1 hour, wherein comparative example No.49, No.50 insulation is 0.5 hour, be cooled to 60 ℃ oil quenching then, and then carry out tempering in insulation water-cooled after 30 minutes under 550 ℃ the temperature condition.Then, each cylinder material 2 is carried out mechanical workout, the summer of making JIS Z2202 defined according to the method for JIS Z2242 defined, is implemented the Charpy impact test under the room temperature than impacting test piece 3.Adopt the absorption merit (J/cm of per unit area as evaluation index this moment 2).
Tension test
To the cylinder material of producing abreast with the drawing-down direction 2, with same method of above-mentioned Charpy impact test and condition under carry out oil quenching and tempering after, the diameter that is processed into parallel portion is that the length of 8mm, parallel portion is the tensile test specimen of 30mm, based on the method for JIS Z2241 defined, carry out the tension test under the room temperature.Adopt yield ratio (=(0.2% yield strength YP)/(tensile strength TS)) as evaluation index this moment.
Above test-results is shown in table 5 and table 6.
Table 5
Figure G2007800109591D00171
Table 6
Figure G2007800109591D00181
No.1 shown in table 1, table 2 and the table 5～42 steel are embodiments of the invention, and the No.43 shown in table 2 and the table 6～51 steel are comparative examples of the present invention.Shown in table 5 and table 6, embodiment No.1～No.42 steel, its evaluation index VL1000, VB_max, impact value (absorption merit) and YP/TS (yield ratio) all demonstrate good value, but the steel of comparative example, at least one above characteristic in these evaluation indexes is poorer than the steel of embodiment.Specifically, comparative example No.43～No.46 steel, total Al content is lower than scope of the present invention, so machinability evaluation index VL1000 and yield ratio (YP/TS) are poorer than the steel of embodiment.In addition, comparative example No.47 steel, total Al content is lower than scope of the present invention terrifically, so solid solution N amount is greater than scope of the present invention, and its machinability (VL1000, VB_max), impact value (Impact Value) and yield ratio (YP/TS) are poorer than the steel of embodiment.
Comparative example No.48 steel, total Al content are greater than scope of the present invention, so the hardness increase, and (VL1000, VB_max) is poor for machinability.Comparative example No.49, No.50 steel, compare with the steel of embodiment, short in the soaking time of separating out easily under 850 ℃ of AlN, so solid solution N amount is greater than scope of the present invention, machinability (VL1000, VB_max) and impact value (Impact Value) are poorer than the steel of embodiment.Comparative example No.51～No.54 steel, Sb content are greater than scope of the present invention, so impact value (Impact Value) is poorer than the steel of embodiment.
Embodiment 2
In the present embodiment, the steel 150kg with the composition shown in vacuum melting furnace refining table 7 and the table 8 carries out forge hot then under 1250 ℃ temperature condition, and it is the cylindrical of 65mm that drawing-down becomes diameter.Then,, carry out machinability test, Charpy impact test and tension test, estimate its characteristic with the method shown in following for each steel of this embodiment and comparative example.Moreover the underscore in table 7 and the table 8 is illustrated in outside the scope of the present invention.
Table 7
Figure G2007800109591D00201
Table 8
Figure G2007800109591D00211
Machinability test
Machinability test, at first for being heated to 1250 ℃ at the hot embodiment of drawing-down and each steel of comparative example of having carried out down, be implemented under 850 ℃ the temperature condition and carry out normalizing in 1 hour, wherein comparative example No.48, No.49, No.97～No.101 carry out normalizing in 0.5 hour, the thermal treatment of air cooling then.Then, each steel after thermal treatment cut machinability evaluation test piece, under the machining condition shown in the table 9, carry out the bit bore test, and carry out vertical turning test, estimated the machinability of each steel of embodiment and comparative example in the condition shown in the table 10.At this moment, as evaluation index, in the bit bore test, adopting machinable is the maximum cutting speed VL1000 of 1000mm to the accumulation hole depth, in vertically turning is tested, adopts the cutter back greatest wear width VBmax after 10 minutes.
Table 9
Figure G2007800109591D00221
Table 10
Charpy impact test
Fig. 1 is the figure that cut position of expression Charpy impact test with test piece.In Charpy impact test, at first as shown in Figure 1, from same method of above-mentioned machinability test and condition under carried out on heat treated each steel 1, cutting diameter is the cylinder material 2 of 25mm, and makes central shaft vertical with the drawing-down direction of steel 1.Then, for each cylinder material 2, carry out under 850 ℃ temperature condition, being incubated 1 hour, wherein comparative example No.48, No.49, No.97～No.101 are incubated 0.5 hour, be cooled to 60 ℃ oil quenching then, and then carry out tempering in insulation water-cooled after 30 minutes under 550 ℃ the temperature condition.Then, each cylinder material 2 is carried out mechanical workout, the summer of making JIS Z2202 defined according to the method for JIS Z2242 defined, is implemented the Charpy impact test under the room temperature than impacting test piece 3.Adopt the absorption merit (J/cm of per unit area as evaluation index this moment 2).
Tension test
Will with same method of above-mentioned Charpy impact test and condition under carried out oil quenching and each cylinder material 2 of tempered, the diameter that is processed into parallel portion is that 8mm, length are the tensile test specimen of 30mm, based on the method for JIS Z 2241 defineds, carry out the tension test under the room temperature.Adopt yield ratio (=(0.2% yield strength YP)/(tensile strength TS)) as evaluation index this moment.
Above test-results is shown in table 11 and table 12.
Table 11
Table 12
Moreover the No.1 steel shown in table 7 and the table 11 are embodiment of claim 1, and the steel of No.2～No.42 are embodiment of claim 2.In addition, the No.52～No.93 shown in table 8 and the table 12 is the embodiment of claim 1.In addition, the steel of comparative example No.43～No.49 satisfy the regulation of claim 2 on S content and Ca content, and the steel of comparative example No.94～No.101 satisfy the regulation of claim 1 on S content and Ca content.
Shown in table 11 and table 12, the steel of embodiment No.1～42 and No.52～No.93, its evaluation index VL1000, VB_max, impact value (absorption merit) and YP/TS (yield ratio) all demonstrate good value, but for the steel of comparative example, at least one above characteristic in these evaluation indexes is poorer than the steel of embodiment.Specifically, the steel of comparative example No.43～No.46, total Al content is lower than scope of the present invention, so the evaluation index VL1000 of machinability and yield ratio (YP/TS) are poorer than the steel of embodiment.In addition, the steel of comparative example No.47, total Al content is lower than scope of the present invention terrifically, so solid solution N amount is greater than scope of the present invention, and its machinability (VL1000, VB_max), impact value (Impact Value) and yield ratio (YP/TS) are poorer than the steel of embodiment.
The steel of comparative example No.48 and No.49, compare with the steel of embodiment, short in the soaking time of separating out easily under 850 ℃ of AlN, so solid solution N amount is greater than scope of the present invention, machinability (VL1000, VB_max) and impact value (Impact Value) are poorer than the steel of embodiment.In addition, the steel of comparative example No.94～No.96, total Al content is lower than scope of the present invention, so machinability (VL1000, VB_max) and yield ratio (YP/TS) are poorer than the steel of embodiment.In addition, the steel of comparative example No.97～No.101, compare with the steel of embodiment, short in the soaking time of separating out easily under 850 ℃ of AlN, therefore solid solution N amount is greater than scope of the present invention, and machinability (VL1000, VB_max) and impact value (Impact Value) are poorer than the steel of embodiment.Utilize possibility on the industry
According to the present invention, the cutting speed zone that can be provided in relative broad range has good machinability and has high impact characteristics simultaneously and the steel for mechanical structure of high yield ratio.
Among the present invention the expression numerical range " more than " and " following " include given figure.

Claims (2)

1. the steel for mechanical structure of machinability and strength characteristics excellence, it is characterized in that, in quality %, contain C:0.1～0.85%, Si:0.01～1.5%, Mn:0.05～2.0%, P:0.005～0.2%, S:0.001～0.15%, comprise whole Al of solid solution Al: surpass 0.1% and be 0.3% below, Sb: be lower than 0.0150% comprising 0% at interior and whole N:0.0035～0.020%, and solid solution N is limited in below 0.0020%, and its surplus is made up of Fe and unavoidable impurities.
2. the steel for mechanical structure of machinability according to claim 1 and strength characteristics excellence, it is characterized in that, in quality %, also contain Ca:0.0003～0.0015%, Ti:0.001～0.1%, Nb:0.005～0.2%, W:0.01～1.0%, V:0.01～1.0%, Mg:0.0001～0.0040%, Zr:0.0003～0.01%, REM:0.0001～0.015%, Sn:0.005～2.0%, Zn:0.0005～0.5%, Te:0.0003～0.2%, Bi:0.005～0.5% and Pb:0.005～0.5%, Cr:0.01～2.0%, and among Mo:0.01～1.0% one or more.
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AU2007342838B2 (en) 2010-04-01
EP2060647A4 (en) 2016-07-13
BR122013026772B1 (en) 2018-01-09
US20090274573A1 (en) 2009-11-05
JP4568362B2 (en) 2010-10-27
CN101410541A (en) 2009-04-15
AU2010200638A1 (en) 2010-03-11
AU2007342838A1 (en) 2008-07-17

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