WO2015146703A1 - Steel material for vacuum carburizing and method for producing same - Google Patents
Steel material for vacuum carburizing and method for producing same Download PDFInfo
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- C—CHEMISTRY; METALLURGY
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
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- 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
- C21D1/06—Surface hardening
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- 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
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
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- C—CHEMISTRY; METALLURGY
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- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/28—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for plain shafts
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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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/32—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for gear wheels, worm wheels, or the like
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
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- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- 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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/20—Carburising
- C23C8/22—Carburising of ferrous surfaces
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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
- C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
- C21D7/04—Modifying the physical properties of iron or steel by deformation by cold working of the surface
- C21D7/06—Modifying the physical properties of iron or steel by deformation by cold working of the surface by shot-peening or the like
Definitions
- the chemical component composition is appropriately adjusted and the average equivalent circle diameter of vanadium carbide is set to a predetermined value or less, so that the surface carburizing strength after vacuum carburizing treatment is excellent, and the vacuum carburizing is performed. And carburized parts excellent in bending fatigue strength after shot peening can be obtained.
- the carburized parts of the present invention are also characterized in that they are obtained by vacuum carburizing.
- vacuum carburization is not performed and gas carburization, gas carbonitriding, or the like is performed, a grain boundary oxide layer is generated on the surface, and surface fatigue strength and bending fatigue strength described later are reduced.
- the surface grain boundary oxide layer depth can be 3 ⁇ m or less.
- Mo 0.3-0.8%
- Mo has the effect of improving the softening resistance by precipitating Mo 2 C during tempering.
- the hardness is maintained by suppressing the softening and pitching. Contributes to improving fatigue strength such as strength.
- Mo also has the effect of improving toughness.
- the Mo amount is set to 0.3% or more.
- the amount of Mo is preferably 0.35% or more, and more preferably 0.4% or more.
- the Mo amount is set to 0.8% or less. Mo amount becomes like this. Preferably it is 0.75% or less, More preferably, it is 0.7% or less.
- N 0.004 to 0.025%
- N forms nitrides with Al and the like, refines crystal grains, and exhibits the effect of improving toughness.
- the N content is set to 0.004% or more.
- the amount of N is preferably 0.0060% or more, and more preferably 0.010% or more.
- coarse nitrides such as Al-based nitrides are generated and do not contribute as pinning particles, which causes crystal grain coarsening. From this point of view, the N content is determined to be 0.025% or less.
- the N amount is preferably 0.020% or less, more preferably 0.017% or less.
- (sigma) (Xmm) means the value of the residual stress in the position of Xmm from the surface.
- Test No. Nos. 3, 5, 14 to 18, 22 to 29, and 31 to 34 are steel materials that satisfy the chemical composition defined in the present invention and are obtained under appropriate hot rolling conditions. Therefore, the average equivalent circle diameter of VC is 25 nm or less, and the steel obtained by vacuum carburizing or the steel obtained by vacuum carburizing and shot peening has a surface hardness when tempered at 400 ° C.
- the surface fatigue strength expressed by 1,000,000 times strength is 3.3 GPa or more. Compared to 1, the surface fatigue strength was 1.20 times or more.
- Test No. Nos. 26 and 31 to 34 are examples in which shot peening was performed under an appropriate condition after vacuum carburization. Since compressive residual stress could be sufficiently applied, bending fatigue strength expressed by 100,000 times strength was obtained.
- No. No. 19 is an example in which the heating temperature before hot rolling was low
- No. 20 is an example in which the heating and holding time before hot rolling was short
- No. 21 is an example in which the heating and holding time before hot rolling was long. In either case, the average equivalent circle diameter of vanadium carbide was increased, resulting in poor surface fatigue strength.
- No. 30 is an example in which gas carburization was performed, and a grain boundary oxide layer was formed, resulting in poor surface fatigue strength.
Abstract
Description
質量%で、
C :0.15~0.35%、
Si:0.6~2.0%、
Mn:0.3~1.3%、
S :0%超、0.020%以下、
P :0%超、0.015%以下、
Cr:0.7~1.7%、
Mo:0.3~0.8%、
V :0.10~0.4%、
Al:0.005~0.05%、
N :0.004~0.025%
を含有し、残部が鉄および不可避不純物からなる真空浸炭用鋼材であって、
バナジウム炭化物の平均円相当径が25nm以下であることを特徴とする真空浸炭用鋼材である。 The present invention that has achieved the above problems
% By mass
C: 0.15-0.35%,
Si: 0.6-2.0%,
Mn: 0.3 to 1.3%,
S: more than 0%, 0.020% or less,
P: more than 0%, 0.015% or less,
Cr: 0.7 to 1.7%,
Mo: 0.3 to 0.8%,
V: 0.10 to 0.4%,
Al: 0.005 to 0.05%,
N: 0.004 to 0.025%
Is a steel material for vacuum carburization consisting of iron and inevitable impurities,
It is a steel material for vacuum carburizing characterized in that the average equivalent circle diameter of vanadium carbide is 25 nm or less.
(a)Nb:0質量%超、0.06質量%以下及びTi:0質量%超、0.2質量%以下の少なくとも1種
(b)B:0質量%超、0.005質量%以下 The present invention preferably further contains one or more of the following (a) and (b).
(A) Nb: more than 0% by mass, 0.06% by mass or less and Ti: more than 0% by mass, 0.2% by mass or less (b) B: more than 0% by mass, 0.005% by mass or less
上記したいずれかに記載の化学成分組成を有する鋼を、
1200℃以上で30~300分保持して分塊圧延し、
熱間圧延前の加熱温度を950℃以上、加熱保持時間を30分~5時間として熱間圧延することを特徴とする真空浸炭用鋼材の製造方法である。 The present invention also includes a method for producing the above-described steel material, and specifically, the production method includes:
Steel having the chemical composition described in any of the above,
Hold it at 1200 ° C or higher for 30 to 300 minutes and perform batch rolling.
A method for producing a steel material for vacuum carburizing, characterized by performing hot rolling at a heating temperature before hot rolling of 950 ° C. or higher and a heating holding time of 30 minutes to 5 hours.
上記したいずれかに記載の化学成分組成を有し、
表面粒界酸化層深さが3μm以下であり、
400℃で焼戻した時の表面硬さがビッカース硬さで600以上である浸炭部品である。該浸炭部品は面疲労強度に優れている。 The present invention also includes a carburized part obtained from the above steel for vacuum carburizing, and specifically, the carburized part is:
Having any of the chemical component compositions described above,
The surface grain boundary oxide layer depth is 3 μm or less,
It is a carburized part whose surface hardness when tempered at 400 ° C. is 600 or more in terms of Vickers hardness. The carburized parts are excellent in surface fatigue strength.
上記したいずれかに記載の化学成分組成を有し、
表面粒界酸化層深さが3μm以下であり、
表面から30μm深さ位置までの残留応力積分値が40MPa・mm以上であり、
400℃で焼戻した時の表面硬さがビッカース硬さで600以上である浸炭部品である。該部品は面疲労強度及び曲げ疲労強度に優れている。 Furthermore, a part obtained by further shot peening the carburized part is also included in the present invention.
Having any of the chemical component compositions described above,
The surface grain boundary oxide layer depth is 3 μm or less,
The residual stress integral value from the surface to the 30 μm depth position is 40 MPa · mm or more,
It is a carburized part whose surface hardness when tempered at 400 ° C. is 600 or more in terms of Vickers hardness. The part is excellent in surface fatigue strength and bending fatigue strength.
上記したいずれかに記載の真空浸炭用鋼材を、真空浸炭、焼入れ焼戻し及びショットピーニングする浸炭部品の製造方法であって、
ショットピーニングの投射材の粒径が0.10~0.5mmであり、
前記投射材の硬さがビッカース硬さで800~1000である面疲労強度及び曲げ疲労強度に優れた浸炭部品の製造方法である。 The present invention also includes a method of manufacturing a part subjected to the above-described shot peening, and specifically the manufacturing method,
A steel material for vacuum carburizing according to any one of the above, vacuum carburizing, quenching and tempering and shot peening carburizing parts manufacturing method,
The particle size of the shot peening projection material is 0.10 to 0.5 mm,
This is a method for manufacturing a carburized part excellent in surface fatigue strength and bending fatigue strength in which the projection material has a Vickers hardness of 800 to 1000.
Cは、鋼材に強度を付与できる元素である。必要な強度を得るため、C量を0.15%以上と定めた。C量は、好ましくは0.17%以上であり、より好ましくは0.19%以上である。一方、C量が過剰になると被削性及び靭性が低下する。従ってC量を0.35%以下と定めた。C量は、好ましくは0.33%以下であり、より好ましくは0.31%以下である。 C: 0.15-0.35%
C is an element that can impart strength to the steel material. In order to obtain the required strength, the C content is set to 0.15% or more. The amount of C is preferably 0.17% or more, and more preferably 0.19% or more. On the other hand, when the amount of C is excessive, machinability and toughness are reduced. Therefore, the C content is set to 0.35% or less. The amount of C is preferably 0.33% or less, and more preferably 0.31% or less.
Siは、焼戻し軟化抵抗向上元素として作用し、歯車などにおいて駆動中に接触部位の温度が上昇した際に、軟化抑制によって硬さを維持し、ピッチング強度などの疲労強度向上、耐摩耗性向上に寄与する。こうした効果を有効に発揮させるため、Si量を0.6%以上と定めた。Si量は、好ましくは0.8%以上であり、より好ましくは1.0%以上である。しかしながら、Si量が過剰になると強度上昇が著しくなって、冷間加工性及び被削性が低下する。そこで、Si量を2.0%以下と定めた。Si量は、好ましくは1.8%以下であり、より好ましくは1.6%以下である。 Si: 0.6-2.0%
Si acts as a temper softening resistance improving element, and when the temperature of the contact part rises during driving in gears, etc., it maintains hardness by suppressing softening, and improves fatigue strength such as pitching strength and wear resistance. Contribute. In order to exhibit such an effect effectively, the Si amount was determined to be 0.6% or more. The amount of Si is preferably 0.8% or more, and more preferably 1.0% or more. However, when the amount of Si becomes excessive, the strength rises remarkably and cold workability and machinability deteriorate. Therefore, the Si amount is set to 2.0% or less. The amount of Si is preferably 1.8% or less, and more preferably 1.6% or less.
Mnは、脱酸剤や脱硫剤、および焼入れ性向上元素として添加される。そのような効果を有効に発揮させるため、Mn量を0.3%以上と定めた。Mn量は、好ましくは0.4%以上であり、より好ましくは0.5%以上である。しかしながら、Mn量が過剰になると、冷間鍛造性や靭性の低下を招くと共に、被削性も劣化する。そこで、Mn量は1.3%以下と定めた。Mn量は、好ましくは1.2%以下であり、より好ましくは1.1%以下である。 Mn: 0.3 to 1.3%
Mn is added as a deoxidizer, desulfurizer, and hardenability improving element. In order to exhibit such an effect effectively, the amount of Mn was determined to be 0.3% or more. The amount of Mn is preferably 0.4% or more, more preferably 0.5% or more. However, when the amount of Mn is excessive, cold forgeability and toughness are lowered and machinability is also deteriorated. Therefore, the amount of Mn is set to 1.3% or less. The amount of Mn is preferably 1.2% or less, more preferably 1.1% or less.
Sは、不可避不純物として鋼中に含まれる元素であり、MnSとして析出し、疲労特性や衝撃特性を低下させるため極力低減することが望ましい。しかしながら、極端に低減することは製鋼コストの増大を招くことになる。こうした観点から、S量を0.020%以下と定めた。S量は、好ましくは0.015%以下であり、より好ましくは0.010%以下である。上述の通り、Sは不可避的に含まれる不純物であり、その量を0%にすることは工業生産上困難であり、S量の下限は0.0005%程度である。 S: more than 0% and 0.020% or less S is an element contained in steel as an unavoidable impurity, and it is desirable to reduce it as much as possible because it precipitates as MnS and deteriorates fatigue characteristics and impact characteristics. However, extremely reducing causes an increase in steelmaking cost. From this point of view, the S content is determined to be 0.020% or less. The amount of S is preferably 0.015% or less, more preferably 0.010% or less. As described above, S is an unavoidable impurity, and it is difficult to make the amount 0% in industrial production, and the lower limit of the amount of S is about 0.0005%.
Pは、不可避不純物として鋼中に含まれる元素であり、粒界に偏析し、加工性や疲労特性を低下させるため極力低減することが望ましい。しかしながら、極端に低減することは製鋼コストの増大を招くことになる。こうした観点から、P量を0.015%以下と定めた。P量は、好ましくは0.010%以下であり、より好ましくは0.008%以下である。上述の通り、Pは不可避的に含まれる不純物であり、その量を0%にすることは工業生産上困難であり、P量の下限は0.0005%程度である。 P: more than 0% and 0.015% or less P is an element contained in steel as an unavoidable impurity, and segregates at the grain boundary, and it is desirable to reduce it as much as possible to reduce workability and fatigue characteristics. However, extremely reducing causes an increase in steelmaking cost. From this point of view, the P content is set to 0.015% or less. The amount of P is preferably 0.010% or less, and more preferably 0.008% or less. As described above, P is an unavoidable impurity, and it is difficult to make the amount 0% in industrial production, and the lower limit of the P amount is about 0.0005%.
Crは、Mnと同様に焼入れ性向上元素として添加され、また焼戻し軟化抵抗元素として作用する。こうした効果を有効に発揮させるため、Cr量を0.7%以上と定めた。Cr量は、好ましくは0.8%以上であり、より好ましくは0.9%以上である。しかしながら、Cr量が過剰になると、冷間鍛造性や靭性の低下を招くと共に、被削性も劣化させる。こうした観点から、Cr量を1.7%以下と定めた。Cr量は、好ましくは1.6%以下であり、より好ましくは1.5%以下である。 Cr: 0.7 to 1.7%
Cr, like Mn, is added as a hardenability improving element and acts as a temper softening resistance element. In order to exhibit such an effect effectively, the Cr content is set to 0.7% or more. The amount of Cr is preferably 0.8% or more, and more preferably 0.9% or more. However, when the amount of Cr becomes excessive, cold forgeability and toughness are lowered and machinability is also deteriorated. From this point of view, the Cr content is set to 1.7% or less. The amount of Cr is preferably 1.6% or less, and more preferably 1.5% or less.
Moは、焼戻し時にMo2Cを析出することで、軟化抵抗を向上させる効果を有し、歯車などにおいて駆動中に接触部位の温度が上昇した際に、軟化抑制によって硬さを維持し、ピッチング強度などの疲労強度向上に寄与する。また、Moは靭性を向上させる効果も有している。こうした効果を有効に発揮させるため、Mo量を0.3%以上と定めた。Mo量は、好ましくは0.35%以上であり、より好ましくは0.4%以上である。一方、Mo量が過剰になると、強度上昇が著しくなって、冷間加工性及び被削性が低下する。そこで、Mo量を0.8%以下と定めた。Mo量は、好ましくは0.75%以下であり、より好ましくは0.7%以下である。 Mo: 0.3-0.8%
Mo has the effect of improving the softening resistance by precipitating Mo 2 C during tempering. When the temperature of the contact part rises during driving in a gear or the like, the hardness is maintained by suppressing the softening and pitching. Contributes to improving fatigue strength such as strength. Mo also has the effect of improving toughness. In order to effectively exhibit such an effect, the Mo amount is set to 0.3% or more. The amount of Mo is preferably 0.35% or more, and more preferably 0.4% or more. On the other hand, when the amount of Mo becomes excessive, the strength rises remarkably and cold workability and machinability deteriorate. Therefore, the Mo amount is set to 0.8% or less. Mo amount becomes like this. Preferably it is 0.75% or less, More preferably, it is 0.7% or less.
Vは、焼戻し時にバナジウム炭化物を析出することで、軟化抵抗を向上させる効果を有し、歯車などにおいて駆動中に接触部位の温度が上昇した際に、軟化抑制によって硬さを維持し、ピッチング強度などの疲労強度向上に寄与する。こうした効果を有効に発揮させるため、V量を0.10%以上と定めた。V量は、好ましくは0.15%以上であり、より好ましくは0.2%以上である。しかしながら、V量が過剰になると強度上昇が著しくなって、冷間加工性及び被削性が低下し、さらに圧延後に粗大なバナジウム炭化物が析出し、真空浸炭処理後の軟化抵抗性向上に寄与しない。そこで、V量を0.4%以下と定めた。V量は、好ましくは0.35%以下であり、より好ましくは0.3%以下である。 V: 0.10 to 0.4%
V has the effect of improving the softening resistance by precipitating vanadium carbide during tempering. When the temperature of the contact part rises during driving in a gear or the like, the hardness is maintained by suppressing the softening, and the pitching strength This contributes to improving fatigue strength. In order to exhibit such an effect effectively, the V amount is set to 0.10% or more. The amount of V is preferably 0.15% or more, and more preferably 0.2% or more. However, when the amount of V is excessive, the strength increases remarkably, cold workability and machinability decrease, and coarse vanadium carbide precipitates after rolling, which does not contribute to the improvement of softening resistance after vacuum carburizing treatment. . Therefore, the V amount is set to 0.4% or less. V amount becomes like this. Preferably it is 0.35% or less, More preferably, it is 0.3% or less.
Alは、脱酸剤であると同時に、微細なAl系窒化物を形成することにより、結晶粒を微細化し、靭性を向上させる効果も有している。こうした効果を有効に発揮させるため、Al量を0.005%以上と定めた。Al量は、好ましくは0.01%以上であり、より好ましくは0.012%以上である。しかしながら、Al量が過剰になると被削性に悪影響を及ぼし、加工性を低下させる他、粗大な窒化物が生成するため、ピンニング粒子として寄与せず、結晶粒粗大化を引き起こすこととなる。こうした観点から、Al量を0.05%以下と定めた。Al量は、好ましくは0.045%以下であり、より好ましくは0.043%以下である。 Al: 0.005 to 0.05%
At the same time as Al is a deoxidizer, it also has the effect of reducing crystal grains and improving toughness by forming fine Al-based nitrides. In order to exhibit such an effect effectively, the Al content is set to 0.005% or more. The amount of Al is preferably 0.01% or more, and more preferably 0.012% or more. However, when the amount of Al is excessive, the machinability is adversely affected, the workability is lowered, and coarse nitrides are generated. Therefore, the Al content does not contribute as pinning particles and causes coarsening of crystal grains. From this point of view, the Al content is determined to be 0.05% or less. The amount of Al is preferably 0.045% or less, and more preferably 0.043% or less.
Nは、Al等と窒化物を形成し、結晶粒を微細化し、靭性を向上させる効果を発揮する。こうした効果を有効に発揮させるため、N量を0.004%以上と定めた。N量は、好ましくは0.0060%以上であり、より好ましくは0.010%以上である。しかしながら、N量が過剰になると、特にAl系窒化物などの粗大な窒化物が生成してピンニング粒子として寄与せず、結晶粒粗大化を引き起こすこととなる。こうした観点から、N量を0.025%以下と定めた。N量は、好ましくは0.020%以下であり、より好ましくは0.017%以下である。 N: 0.004 to 0.025%
N forms nitrides with Al and the like, refines crystal grains, and exhibits the effect of improving toughness. In order to exhibit such an effect effectively, the N content is set to 0.004% or more. The amount of N is preferably 0.0060% or more, and more preferably 0.010% or more. However, when the amount of N is excessive, coarse nitrides such as Al-based nitrides are generated and do not contribute as pinning particles, which causes crystal grain coarsening. From this point of view, the N content is determined to be 0.025% or less. The N amount is preferably 0.020% or less, more preferably 0.017% or less.
NbおよびTiは、浸炭後の結晶粒を微細化し、鋼材の靭性を向上させると共に、曲げ疲労強度を向上させるのに有用である。これらの元素は、必要に応じていずれか1種または2種を含有することによって上記の効果が発揮される。こうした効果を有効に発揮させるため、Nb量は0.01%以上が好ましく、Ti量は0.005%以上が好ましい。好ましいNb量及びTi量は、いずれも0.015%以上である。しかしながら、これらの元素が過剰になると、その効果が飽和するだけでなく、粗大な析出物を形成し、強度を低下させる。そこで、Nb量は0.06%以下が好ましく、Ti量は0.2%以下が好ましい。Nb量は0.05%以下がより好ましく、Ti量は0.1%以下がより好ましく、0.08%以下が更に好ましい。 Nb: more than 0%, 0.06% or less and Ti: more than 0%, 0.2% or less Nb and Ti refine crystal grains after carburization, improve the toughness of steel, and bend Useful for improving fatigue strength. These elements exhibit the above effects by containing either one or two of them as necessary. In order to effectively exhibit these effects, the Nb content is preferably 0.01% or more, and the Ti content is preferably 0.005% or more. The preferable Nb amount and Ti amount are both 0.015% or more. However, when these elements become excessive, not only the effect is saturated, but also coarse precipitates are formed and the strength is lowered. Therefore, the Nb content is preferably 0.06% or less, and the Ti content is preferably 0.2% or less. The Nb content is more preferably 0.05% or less, the Ti content is more preferably 0.1% or less, and even more preferably 0.08% or less.
Bは、浸炭処理における焼入れ性を高める作用を有し、また粒界を強化して曲げ疲労強度を向上させる元素である。Bは微量添加により焼入れ性の向上が可能であるため、加工性等への影響が低い。こうした作用を有効に発揮させるため、B量は0.0005%以上が好ましく、より好ましくは0.0008%以上である。しかしながら、B量が過剰になるとNとの結合によりBNを生成して、浸炭部品の強度が低下する。従って、B量は0.005%以下が好ましく、より好ましくは0.0045%以下であり、更に好ましくは0.0040%以下である。 B: More than 0% and 0.005% or less B is an element that has the effect of enhancing the hardenability in the carburizing treatment and also strengthens the grain boundary to improve the bending fatigue strength. Since B can improve the hardenability by adding a trace amount, the influence on workability and the like is low. In order to effectively exhibit these actions, the B content is preferably 0.0005% or more, more preferably 0.0008% or more. However, when the amount of B is excessive, BN is generated by the combination with N, and the strength of the carburized component is lowered. Accordingly, the B content is preferably 0.005% or less, more preferably 0.0045% or less, and still more preferably 0.0040% or less.
なお、比較となるガス浸炭は、カーボンポテンシャルCp:0.8%の浸炭ガス雰囲気中、930℃で浸炭処理した後、油冷し、更に170℃で2時間の焼戻し処理を行った。 About each obtained hot-rolled material, the magnitude | size of vanadium carbide was measured by the method of following (1). Further, after the above hot-rolled material was subjected to vacuum carburizing or gas carburizing under the carburizing conditions shown in Tables 2 and 3, Test No. For Nos. 26 to 34, shot peening was performed using a projection material having the particle size and hardness shown in Table 3 to prepare test pieces. The vacuum carburizing treatment is performed in the temperature range of 930 to 980 ° C shown in Tables 2 and 3, and then cooled to 780 to 880 ° C and then poured into oil at 60 to 130 ° C and quenched. And tempering by reheating to 170 ° C. Shot peening was performed using the projection material shown in Table 3 at a projection pressure of 0.4 MPa and a coverage of 400% or more. The blasting material was classified by sieving, in a range of 0.05 to 0.06 mm, 0.11 to 0.13 mm, 0.18 to 0.21 mm, 0.36 to 0.43 mm and 0.60 to 0.71 mm. Particle size was used.
In addition, the gas carburizing used as a comparison was carburized at 930 ° C. in a carburizing gas atmosphere with a carbon potential Cp of 0.8%, then cooled with oil, and further tempered at 170 ° C. for 2 hours.
熱間圧延材の、D/4位置を横断面に切出し、研磨した後、カーボン蒸着を行い、FE-TEM(Field-Emission Transmission Electron Microscope)によるレプリカ観察を実施した。前記Dは圧延材の直径を意味する。この際、TEMのEDX(Energy Dispersive X-ray Analysis)によりV及びCの検出される析出物を特定し、10万倍の倍率にて1.0μm×1.2μmの視野の観察を行った。観察は任意の3視野について行い、観察されたバナジウム炭化物の円相当径の算術平均値を、バナジウム炭化物の平均円相当径とした。なお、FE-TEMの測定限界から、測定対象としたバナジウム炭化物の大きさの下限は円相当径でおよそ1nm程度である。 (1) Measurement of size of vanadium carbide in hot-rolled material The D / 4 position of the hot-rolled material is cut into a cross section and polished, and then carbon deposition is performed, and FE-TEM (Field-Emission Transmission Electron Microscope). ) Replica observation was carried out. Said D means the diameter of a rolling material. At this time, precipitates in which V and C were detected were identified by TEM EDX (Energy Dispersive X-ray Analysis), and a 1.0 μm × 1.2 μm visual field was observed at a magnification of 100,000 times. Observation was performed for three arbitrary visual fields, and the arithmetic average value of the observed equivalent circle diameter of vanadium carbide was defined as the average equivalent circle diameter of vanadium carbide. From the measurement limit of FE-TEM, the lower limit of the size of the vanadium carbide to be measured is about 1 nm in terms of the equivalent circle diameter.
上記した熱間圧延材の表面を研磨してφ26.02mmとしてから浸炭し、再度研磨してφ26mmとした。試験No.26~34についてはさらにショットピーニングし、400℃焼戻し硬さの測定用の試験片とした。試験No.1~25については浸炭後の試験片、No.26~34については浸炭及びショットピーニング後の試験片について、400℃で3時間焼戻しを行い、横断面において表面から50μm位置について、ビッカース硬さ計で硬さを測定した。ビッカース硬さ計の試験荷重は300gfとし、5箇所測定してその算術平均値を求め、これを各試験片の400℃焼戻し硬さとした。 (2) Measurement of tempering hardness at 400 ° C. The surface of the hot-rolled material described above was polished to φ26.02 mm, carburized, and polished again to φ26 mm. Test No. Samples 26 to 34 were further shot peened and used as test pieces for measuring 400 ° C. tempering hardness. Test No. For Nos. 1 to 25, specimens after carburization, No. For 26 to 34, the specimens after carburization and shot peening were tempered at 400 ° C. for 3 hours, and the hardness was measured with a Vickers hardness meter at a position of 50 μm from the surface in the cross section. The test load of the Vickers hardness tester was 300 gf, and five points were measured to obtain the arithmetic average value. This was the 400 ° C. tempered hardness of each test piece.
後述する図1の4点曲げ試験片を浸炭し、試験No.26~34についてはさらにショットピーニングし、残留応力測定用の試験片とした。試験No.1~25については浸炭後の試験片、No.26~34については浸炭及びショットピーニング後の試験片について、PSPC(Position-Sensitive Proportional Counter)微小部X線応力測定装置を用いて、試験片のノッチ底表面からそれぞれ10μm、20μm、30μmの位置の残留応力を測定し、下記の計算式によって表面から30μm深さ位置までの残留応力積分値を算出した。PSPC微小部X線応力測定装置の測定条件は、コリメーター径:φ1mm、測定部位:軸方向中央位置、測定方向:円周方向である。
表面から30μm深さ位置までの残留応力積分値σ
={σ(0mm)+σ(0.01mm)}/2×0.01mm
+{σ(0.01mm)+σ(0.02mm)}/2×0.01mm
+{σ(0.02mm)+σ(0.03mm)}/2×0.01mm
但し、σ(Xmm)は、表面からXmmの位置での残留応力の値を意味する。 (3) Measurement of integrated value of residual stress at 30 μm depth from the surface A 4-point bending test piece of FIG. Samples 26 to 34 were further shot peened to obtain test pieces for residual stress measurement. Test No. For Nos. 1 to 25, specimens after carburization, No. For Nos. 26 to 34, the specimens after carburization and shot peening were measured at positions of 10 μm, 20 μm, and 30 μm from the notch bottom surface of the specimens using a PSPC (Position-Sensitive Proportional Counter) micro part X-ray stress measuring device Residual stress was measured, and the integrated value of residual stress from the surface to the 30 μm depth position was calculated by the following formula. The measurement conditions of the PSPC minute part X-ray stress measurement apparatus are collimator diameter: φ1 mm, measurement site: axial center position, measurement direction: circumferential direction.
Residual stress integrated value from surface to 30 μm depth σ
= {Σ (0 mm) + σ (0.01 mm)} / 2 × 0.01 mm
+ {Σ (0.01 mm) + σ (0.02 mm)} / 2 × 0.01 mm
+ {Σ (0.02 mm) + σ (0.03 mm)} / 2 × 0.01 mm
However, (sigma) (Xmm) means the value of the residual stress in the position of Xmm from the surface.
上記した熱間圧延材の表面を研磨してφ26.02mmとしてから浸炭し、再度研磨してφ26mmとした。試験No.26~34についてはさらにショットピーニングし、試験片とした。試験No.1~25については浸炭後の試験片、No.26~34については浸炭及びショットピーニング後の試験片について、圧延方向に垂直に切出し、樹脂に埋め込んで研磨した後、試験片の最表面を光学顕微鏡を用いて倍率1000倍で観察し、粒界酸化層の最も深い位置の深さを測定した。 (4) Measurement of depth of surface grain boundary oxide layer The surface of the hot-rolled material described above was polished to φ26.02 mm, carburized, and polished again to φ26 mm. Test No. Samples 26 to 34 were further shot peened to obtain test pieces. Test No. For Nos. 1 to 25, specimens after carburization, No. For Nos. 26 to 34, the carburized and shot peened specimens were cut out perpendicular to the rolling direction, embedded in a resin and polished, and then the outermost surface of the specimen was observed with an optical microscope at a magnification of 1000 times. The depth of the deepest position of the oxide layer was measured.
上記(4)と同様の試験片を準備し、得られた試験片を、面圧:2.7、3.0、3.3GPa、回転数:1500rpm、すべり率:-40%、オートマチックオイル使用の条件でローラーピッチング試験を行って、応力S-繰返し数N線図(以下、S-N線図)を作成し、100万回強度によりピッチング強度を評価した。なお、前記したオートマチックオイルの油温は80℃であり、前記100万回強度とは、100万回試験した際に破損しない最大の応力を意味する。このとき用いた相手ローラは、SUJ2からなる調質品であって、表面硬さ:HV700、クラウニングR:150mmであるものを用いた。 (5) Evaluation of roller pitting fatigue characteristics A test piece similar to the above (4) was prepared, and the obtained test piece was subjected to surface pressure: 2.7, 3.0, 3.3 GPa, rotation speed: 1500 rpm, and slip. Roller pitching test was performed under the conditions of rate: -40%, using automatic oil, stress S-repetition number N diagram (hereinafter referred to as SN diagram) was created, and the pitching strength was evaluated by the strength of 1,000,000 times. . The above-mentioned automatic oil has an oil temperature of 80 ° C., and the “one million times strength” means the maximum stress that is not damaged when tested one million times. The counter roller used at this time was a tempered product made of SUJ2, which had a surface hardness of HV700 and a crowning R of 150 mm.
上記した熱間圧延材から図1に示す形状の試験片を切出してから浸炭し、試験No.26~34についてはさらにショットピーニングし、曲げ疲労試験用の試験片とした。この試験片を用い、図2に示す通り、4点支持となる治具によって、周波数20Hz、繰返し負荷応力の最大応力:1371、1523、1675、1828MPaの条件で、S-N線図を作成し、このS-N線図に基づいて図3に示す通り10万回強度を求め、その値を曲げ疲労強度とした。 (6) Evaluation of bending fatigue characteristics A test piece having the shape shown in FIG. Samples 26 to 34 were further shot peened to obtain test pieces for a bending fatigue test. Using this test piece, as shown in FIG. 2, an SN diagram was created by using a jig that supports four points under the conditions of a frequency of 20 Hz and a maximum stress of repeated load stress of 1371, 1523, 1675, and 1828 MPa. Based on this SN diagram, the strength was determined 100,000 times as shown in FIG. 3, and the value was taken as the bending fatigue strength.
The carburized parts obtained by using the steel for vacuum carburizing according to the present invention are suitable for gears and shafts used in automobiles, construction machines, and other various industrial machines, and are industrially useful.
Claims (6)
- 質量%で、
C :0.15~0.35%、
Si:0.6~2.0%、
Mn:0.3~1.3%、
S :0%超、0.020%以下、
P :0%超、0.015%以下、
Cr:0.7~1.7%、
Mo:0.3~0.8%、
V :0.10~0.4%、
Al:0.005~0.05%、
N :0.004~0.025%
を含有し、残部が鉄および不可避不純物からなる真空浸炭用鋼材であって、
バナジウム炭化物の平均円相当径が25nm以下であることを特徴とする真空浸炭用鋼材。 % By mass
C: 0.15-0.35%,
Si: 0.6-2.0%,
Mn: 0.3 to 1.3%,
S: more than 0%, 0.020% or less,
P: more than 0%, 0.015% or less,
Cr: 0.7 to 1.7%,
Mo: 0.3 to 0.8%,
V: 0.10 to 0.4%,
Al: 0.005 to 0.05%,
N: 0.004 to 0.025%
Is a steel material for vacuum carburization consisting of iron and inevitable impurities,
A steel material for vacuum carburizing, wherein an average equivalent circle diameter of vanadium carbide is 25 nm or less. - 以下の(a)、(b)のいずれかに属する1種以上を更に含有する請求項1に記載の真空浸炭用鋼材。
(a)Nb:0質量%超、0.06質量%以下及びTi:0質量%超、0.2質量%以下の少なくとも1種
(b)B:0質量%超、0.005質量%以下 The steel material for vacuum carburizing according to claim 1, further comprising one or more of the following (a) and (b).
(A) Nb: more than 0% by mass, 0.06% by mass or less and Ti: more than 0% by mass, 0.2% by mass or less (b) B: more than 0% by mass, 0.005% by mass or less - 請求項1または2に記載の化学成分組成を有する鋼を、
1200℃以上で30~300分保持して分塊圧延し、
熱間圧延前の加熱温度を950℃以上、加熱保持時間を30分~5時間として熱間圧延することを特徴とする真空浸炭用鋼材の製造方法。 Steel having the chemical composition according to claim 1 or 2,
Hold it at 1200 ° C or higher for 30 to 300 minutes and perform batch rolling.
A method for producing a steel material for vacuum carburizing, characterized by hot rolling at a heating temperature before hot rolling of 950 ° C. or higher and a heating holding time of 30 minutes to 5 hours. - 請求項1または2に記載の化学成分組成を有し、
表面粒界酸化層深さが3μm以下であり、
400℃で焼戻した時の表面硬さがビッカース硬さで600以上であることを特徴とする面疲労強度に優れた浸炭部品。 The chemical component composition according to claim 1 or 2,
The surface grain boundary oxide layer depth is 3 μm or less,
A carburized part excellent in surface fatigue strength, wherein the surface hardness when tempered at 400 ° C. is 600 or more in terms of Vickers hardness. - 請求項1または2に記載の化学成分組成を有し、
表面粒界酸化層深さが3μm以下であり、
表面から30μm深さ位置までの残留応力積分値が40MPa・mm以上であり、
400℃で焼戻した時の表面硬さがビッカース硬さで600以上であることを特徴とする面疲労強度及び曲げ疲労強度に優れた浸炭部品。 The chemical component composition according to claim 1 or 2,
The surface grain boundary oxide layer depth is 3 μm or less,
The residual stress integral value from the surface to the 30 μm depth position is 40 MPa · mm or more,
A carburized part excellent in surface fatigue strength and bending fatigue strength, wherein the surface hardness when tempered at 400 ° C is 600 or more in terms of Vickers hardness. - 請求項1または2に記載の鋼材を、真空浸炭、焼入れ焼戻し及びショットピーニングする浸炭部品の製造方法であって、
ショットピーニングの投射材の粒径が0.10~0.5mmであり、
前記投射材の硬さがビッカース硬さで800~1000であることを特徴とする面疲労強度及び曲げ疲労強度に優れた浸炭部品の製造方法。 A steel material according to claim 1 or 2 is a carburized part manufacturing method for vacuum carburizing, quenching and tempering and shot peening,
The particle size of the shot peening projection material is 0.10 to 0.5 mm,
A method for producing a carburized part excellent in surface fatigue strength and bending fatigue strength, wherein the projection material has a Vickers hardness of 800 to 1000.
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JP6929535B2 (en) * | 2017-05-25 | 2021-09-01 | 株式会社不二製作所 | Surface treatment method for steel products |
EP3950993A4 (en) * | 2019-03-29 | 2022-10-26 | Nippon Steel Corporation | Carburized part and method for manufacturing same |
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JPH04201128A (en) * | 1990-11-30 | 1992-07-22 | Daido Steel Co Ltd | Manufacture of high bearing part |
JP2003193137A (en) * | 2001-12-25 | 2003-07-09 | Nippon Steel Corp | Carburized and quenched member and production method therefor |
JP2006183095A (en) * | 2004-12-27 | 2006-07-13 | Nippon Steel Corp | Method for producing gear excellent in fatigue strength on tooth surface |
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JP2005163148A (en) | 2003-12-04 | 2005-06-23 | Sanyo Special Steel Co Ltd | Case hardening steel for high strength gear |
DE102005061946B4 (en) * | 2004-12-27 | 2013-03-21 | Nippon Steel Corp. | Case hardened steel having excellent tooth surface fatigue strength, gear using the same, and methods of making same |
JP4853366B2 (en) | 2007-04-13 | 2012-01-11 | 住友金属工業株式会社 | Steel carburized or carbonitrided parts with shot peening |
WO2009025659A1 (en) * | 2007-08-17 | 2009-02-26 | Gkn Sinter Metals, Llc | Variable case depth powder metal gear and method thereof |
KR20120012837A (en) * | 2010-03-10 | 2012-02-10 | 신닛뽄세이테쯔 카부시키카이샤 | Carburized steel component having excellent low-cycle bending fatigue strength |
JP5135563B2 (en) * | 2011-02-10 | 2013-02-06 | 新日鐵住金株式会社 | Carburizing steel, carburized steel parts, and manufacturing method thereof |
JP5620336B2 (en) * | 2011-05-26 | 2014-11-05 | 新日鐵住金株式会社 | Steel parts for high fatigue strength and high toughness machine structure and manufacturing method thereof |
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2014
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2015
- 2015-03-17 MX MX2016012061A patent/MX2016012061A/en unknown
- 2015-03-17 CN CN201710880483.2A patent/CN107653420A/en active Pending
- 2015-03-17 KR KR1020167028788A patent/KR101860658B1/en active IP Right Grant
- 2015-03-17 CN CN201580014824.7A patent/CN106103777B/en not_active Expired - Fee Related
- 2015-03-17 WO PCT/JP2015/057833 patent/WO2015146703A1/en active Application Filing
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Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
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JPH04201128A (en) * | 1990-11-30 | 1992-07-22 | Daido Steel Co Ltd | Manufacture of high bearing part |
JP2003193137A (en) * | 2001-12-25 | 2003-07-09 | Nippon Steel Corp | Carburized and quenched member and production method therefor |
JP2006183095A (en) * | 2004-12-27 | 2006-07-13 | Nippon Steel Corp | Method for producing gear excellent in fatigue strength on tooth surface |
Also Published As
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CN107653420A (en) | 2018-02-02 |
KR20160133549A (en) | 2016-11-22 |
TWI544088B (en) | 2016-08-01 |
CN106103777A (en) | 2016-11-09 |
TW201540849A (en) | 2015-11-01 |
MX2016012061A (en) | 2017-01-19 |
CN106103777B (en) | 2018-07-27 |
KR101860658B1 (en) | 2018-05-23 |
JP6301694B2 (en) | 2018-03-28 |
JP2015183227A (en) | 2015-10-22 |
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