JPWO2016148206A1 - Age-hardening steel and method for producing parts using age-hardening steel - Google Patents

Abstract

Provided is an age-hardenable steel having a low hardness after hot forging, providing machine parts with desired fatigue strength and yield strength by aging treatment, and having high toughness after aging treatment. C: 0.09-0.20%, Si: 0.01-0.40%, Mn: 1.5-2.5%, S: 0.001-0.045%, Cr: 1.00% Over 2.00% or less, Al: 0.001 to 0.060%, V: 0.22 to 0.55%, and N: over 0.0080 to 0.0170% or less, with the balance being Fe And impurities. The area ratio of the bainite structure is 80% or more. The effective V ratio (V solid solution amount / V total amount) is 0.9 or more. P and Ti in the impurities are P: 0.03% or less and Ti: less than 0.005%. The chemical composition has the following F1 of 1.00 or less and the following F2 of 0.30 or more. F1 = C + 0.1 × Si + 0.2 × Mn + 0.15 × Cr + 0.35 × VF2 = −4.5 × C + Mn + Cr−3.5 × V

Description

  The present invention relates to age hardenable steel. More specifically, after being processed into a predetermined shape by hot forging and cutting, an age hardening treatment (hereinafter simply referred to as “aging treatment”) is performed, and desired strength and toughness are ensured by the aging treatment. It relates to steel for manufacturing machine parts for automobiles, industrial machinery and construction machinery. The present invention also relates to a method for manufacturing a part using such age-hardening steel.

  High fatigue strength is required for machine parts such as automobiles, industrial machines, and construction machines from the viewpoints of higher engine output and lighter weight aimed at improving fuel efficiency. If the steel only has a high fatigue strength, it can be easily achieved by increasing the hardness of the steel using an alloy element and / or heat treatment. However, in general, a machine part is formed by hot forging and then finished into a predetermined product shape by cutting. For this reason, the steel used as the material for the machine parts must have sufficient machinability as well as high fatigue strength.

  In general, the higher the hardness of the material, the better the fatigue strength. On the other hand, among the machinability, cutting resistance and tool life tend to be inferior as the hardness of the material increases. Furthermore, among the components that make up the engine, it is necessary that the precision-shaped mechanical components do not change dimensions during use. These precision-shaped machine parts may be momentarily subjected to a higher load than that normally used depending on the usage environment. Therefore, the yield strength is also necessary.

  Therefore, in order to combine fatigue strength, yield strength, and machinability, hardness can be kept low at the molding stage where good machinability is required, while strength is required by applying an aging treatment thereafter. Various techniques have been disclosed that can increase the hardness in the final product stage.

  For example, in JP-A-2006-37177 (Patent Document 1), after rolling, forging, or solution treatment, steel containing an amount in which Mo and V, which are precipitation strengthening elements, are limited by a specific relational expression is disclosed. The temperature is between 800 ° C. and 300 ° C., and is cooled at an average cooling rate of 0.05 to 10 ° C./second. Before the aging treatment, the area ratio of the bainite structure is 50% or more and the hardness is 40 HRC or less. There is disclosed “age-hardening steel” characterized in that the aging treatment increases the hardness by 7 HRC or more than the hardness before the aging treatment.

  In Japanese Patent Application Laid-Open No. 2011-236451 (Patent Document 2), as steel that is excellent in hot forgeability and machinability after hot forging and can be strengthened by age hardening after machining, Bainite steel containing specific amounts of Mo and V as strengthening elements is disclosed.

  In JP 2000-17374 A (Patent Document 3), as an age-hardening type high-strength bainitic steel for hot forging, steel containing Mo and V is hot-rolled or hot forged, and then according to the steel components. Cooling is performed, the hardness is 400 HV or less, the structure is 70% or more of the bainite ratio, and the prior austenite crystal grain size is 80 μm or less. Then, cutting or plastic working is added as necessary, and further aging treatment is performed. Therefore, an age-hardening type high-strength bainitic steel has been proposed in which the yield point or 0.2% proof stress is 900 MPa or more.

  In JP 2013-245363 A (Patent Document 4), after the hot forging, the content of the alloy element is adjusted so as to satisfy a specific parameter formula, so that the content of Mo is relatively reduced. In the steel, the hardness before the aging treatment is 290 HV or less and the hardness after the aging treatment is 325 HV or more, which can be expected to satisfy both high machinability and high fatigue strength.

  International Publication No. 2012/161323 (Patent Document 5) optimizes the shape of V carbonitride having precipitation strengthening ability and the shape of bainite structure by cooling and heat treatment after hot forging, machinability, fatigue A machine structural steel component having both strength and toughness is disclosed.

  Japanese Patent Laid-Open No. 2013-213254 (Patent Document 6) is excellent in cold forgeability and chip disposal after cold forging, and has high core hardness, high surface hardness and deep effective hardening in cold forged and nitrided parts. A steel for cold forging and nitriding that can have a layer depth is disclosed.

  High fatigue strength and yield strength can be obtained by precipitating fine secondary phases in steel by aging treatment. However, the toughness of steel strengthened by aging treatment deteriorates.

  Steel with degraded toughness is more susceptible to notches. As the notch sensitivity increases, the fatigue strength of steel is more susceptible to fine surface flaws.

  Moreover, once a fatigue crack occurs in steel with low toughness, the crack progresses quickly and the fracture becomes large.

  Furthermore, if the toughness of the steel becomes too low, it becomes difficult to correct the strain caused by hot forging cold.

  The steel disclosed in Patent Document 1 can obtain high age-hardening ability by adjusting the content of the alloy element so as to satisfy a specific parameter formula, but the toughness is not considered at all. .

  The steel disclosed in Patent Document 2 adjusts the content of the alloy element so as to satisfy a specific parameter formula, so that the content of Mo is relatively low, and after aging treatment after hot forging and before aging treatment. The hardness is 300 HV or less, and the hardness after aging treatment is 300 HV or more. However, there has not been a sufficient effort to increase toughness after aging treatment.

  The steel disclosed in Patent Document 3 has a C content as low as 0.06 to 0.20%, but because the V content is very high as 0.51 to 1.00%, it is age hardened. However, it is not excellent in toughness.

  The steel disclosed in Patent Document 4 is not sufficiently devised to increase the toughness and yield strength after aging treatment.

  The steel disclosed in Patent Document 5 is not sufficiently devised to increase the yield strength after aging treatment.

  Since the steel disclosed in Patent Document 6 has a low N content, the formation of nitrides is insufficient, and as a result, excellent yield strength has not been obtained.

Accordingly, an object of the present invention is to provide an age-hardening steel that satisfies the following <1> to <3>.
<1> Hardness after hot forging related to cutting resistance and tool life is low. In the following description, the hardness after hot forging is referred to as “hardness before aging treatment”.
<2> A machine part can have desired fatigue strength and yield strength by aging treatment.
<3> High toughness after aging treatment.

  Specifically, the object of the present invention is to provide a JIS No. 14A tensile test having a hardness before aging treatment of 340 HV or less, a fatigue strength described later after aging treatment of 480 MPa or more, and a φ6 parallel portion. A tensile test using a piece was performed, the 0.2% proof stress obtained by the offset method with the specified plastic strain amount being 0.2% was 800 MPa or more, and a notch depth of 2 mm described in JIS Z 2242 and It is to provide an age-hardening steel in which the absorbed energy at 20 ° C. after aging treatment evaluated by a Charpy impact test performed using a standard test piece with a U-notch having a notch bottom radius of 1 mm is 25 J or more.

[Knowledge (a) to (d)]
In order to solve the above problems, the present inventors relate to a value calculated by an equation using a chemical composition, a structure, an effective V ratio (V solid solution amount / V total amount), and a specific element content. A survey was conducted. Specifically, the conditions for obtaining good toughness were investigated even in a steel having high fatigue strength and yield strength by precipitating a fine secondary phase in the steel by aging. As a result, the following findings (a) to (d) were obtained.

(A) Limitation of chemical composition (C, V, Mo, Ti) Elements that degrade toughness after aging treatment are C, V, Mo, and Ti. Among these, Ti combines with N and / or C to form TiN and / or TiC. When TiN and / or TiC is precipitated, the fatigue strength may be increased, but the toughness is greatly reduced. Compared with the same precipitation strengthening elements V and Mo, the strength of the effect of deteriorating the toughness of Ti is extremely large. Therefore, Ti must be limited as much as possible.

  C forms cementite in steel and can be a starting point of cleavage fracture. Even when steel containing an excessive amount of V or Mo with respect to the amount of C is aged, some cementite remains. V and Mo also precipitate the carbides on the same crystal plane of the matrix by aging treatment, thereby promoting the progress of cleavage fracture and degrading toughness. Therefore, in order to improve toughness, it is necessary to reduce the contents of C, V and Mo.

(B) Structure limitation In order to increase toughness, it is necessary to make most of the structure fine bainite. Furthermore, it is indispensable to improve the toughness to increase the orientation difference between the blocks constituting the bainite. If the azimuth difference between the blocks is small, the effect of increasing toughness cannot be sufficiently obtained even if the block particle size is reduced. In order to increase the misorientation between blocks, it is necessary to increase the driving force during the bainite transformation and promote the nucleation of blocks with a large misorientation. In order to obtain these effects, the content of C, Mn, Cr, and Mo may be increased.

  However, C and Mo have the effect of reducing the toughness by refining the structure and increasing the toughness and by precipitating as cementite or carbide. Overall, C greatly deteriorates toughness, and Mo slightly deteriorates toughness.

(C) Limitation of effective V ratio In order to make maximum use of precipitation strengthening by V, it is necessary to limit the effective V ratio defined as the amount of V solid solution with respect to the total amount of V. A small effective V ratio means that the ratio of the amount of V contributing to precipitation strengthening is small and the strengthening ability is small, which is not preferable. There is no upper limit to the effective V ratio, and the closer to 1, the better.

(D) Limitation of values calculated by mathematical formulas using specific element contents, and limitation of Ti amount In order to impart sufficient toughness to age-hardenable steel having high strength, C, Mn, Cr It is necessary to control the content of V and Mo so that the value represented by the formula (2) or (2 ′) indicating the toughness index after aging treatment described later is a specific value or more. In order to prevent inclusions and precipitates harmful to toughness from being contained in the steel, it is necessary to make the Ti content below a specific value.

[Knowledge (e) to (g)]
Next, the present inventors further investigated and examined the values calculated by the mathematical composition using the chemical composition and the content of a specific element. Specifically, various components of the steel that can secure toughness after aging were adjusted, and the conditions related to the age-hardening ability represented by the hardness before aging and the hardness after aging, and the difference between them were investigated. . As a result, the following findings (e) to (g) were obtained.

(E) Limitation of value calculated by mathematical formula using content of specific element The content of C, Si, Mn, Cr, V and Mo is expressed by formula (1) or formula (1 ′) described later. If the value to be controlled is controlled to be in a specific range, it is possible to prevent the hardness before the aging treatment from becoming excessively high. Therefore, machinability capable of industrial mass production can be expected when cutting is performed under various conditions.

(F) Limitation of chemical composition (M, V, C) When the contents of Mo, V, and C are reduced in order to increase the toughness after aging, the driving force for precipitation of V carbonitride during aging is reduced. Therefore, the fine precipitate produced | generated by aging decreases, and the hardness and yield strength after aging become low.

(G) Limitation of chemical composition (Mn, Cr) When the contents of Mn and Cr are increased in order to increase the toughness after aging, the hardenability increases and the hardness before aging becomes harder. In such a structure, the recovery of the structure is likely to proceed by aging, so that the increase in hardness due to aging tends to be small. When the hardenability is increased, the movable dislocation density remaining in the base material after aging is likely to increase, so that it is difficult to obtain a high yield strength.

[Knowledge (h) to (j)]
Subsequently, the inventors further investigated and investigated the chemical composition. Specifically, in order to increase the toughness after aging, the content of C, V and Mo is decreased, and even if the content of Mn and Cr is increased, a sufficient amount of precipitation strengthening particles are precipitated, and sufficient age hardening is achieved. In order to obtain high performance and high yield strength, it was noted that the precipitation strengthening ability per unit V amount needs to be increased. And the present inventors examined various methods for increasing the precipitation strengthening ability by V, and obtained the following knowledge (h) to (j).

(H) Limitation of chemical composition (C, N) In order to make maximum use of precipitation strengthening by V, the driving force for precipitation of V carbonitride may be increased. For that purpose, it is necessary to sufficiently secure the amount of C and N that can be used for the precipitation of V carbonitride within a range that does not impair toughness.

(I) Limitation of chemical composition (N) Since the bonding force between N and V is larger than the bonding force between C and V, the effect of promoting the precipitation of V carbonitride is greater in N than in C.

(J) Limitation of chemical composition (C, N) When the contents of C and N are excessive, V does not form a solution even by heating during hot forging, or precipitates in the austenite region during forging. I'll be relaxed. Therefore, if the contents of C and N are excessively increased, the precipitation strengthening ability is conversely reduced.

  The present invention has been made on the basis of the above findings (a) to (j), and the gist thereof is as follows.

[1] By mass%, C: 0.09 to 0.20%, Si: 0.01 to 0.40%, Mn: 1.5 to 2.5%, S: 0.001 to 0.045% Cr: more than 1.00% and 2.00% or less, Al: 0.001 to 0.060%, V: 0.22 to 0.55%, and N: more than 0.0080 to 0.0170 % And the balance consists of Fe and impurities, P and Ti in the impurities are P: 0.03% or less and Ti: less than 0.005%,
The area ratio of the bainite structure is 80% or more,
The effective V ratio (V solid solution amount / V total amount) is 0.9 or more,
Furthermore, the age-hardenable steel has a chemical composition in which F1 represented by the following formula (1) is 1.00 or less and F2 represented by the formula (2) is 0.30 or more.
F1 = C + 0.1 × Si + 0.2 × Mn + 0.15 × Cr + 0.35 × V (1)
F2 = −4.5 × C + Mn + Cr−3.5 × V (2)
The element symbols in the above formulas (1) and (2) mean the content in mass% of the element.

[2] By mass%, C: 0.09 to 0.20%, Si: 0.01 to 0.40%, Mn: 1.5 to 2.5%, S: 0.001 to 0.045% Cr: more than 1.00% and 2.00% or less, Al: 0.001-0.060%, V: 0.22-0.55%, Mo: 0.9% or less, and N: More than 0.0080 and 0.0170% or less, the balance consists of Fe and impurities, P and Ti in the impurities are P: 0.03% or less and Ti: less than 0.005%,
The area ratio of the bainite structure is 80% or more,
The effective V ratio (V solid solution amount / V total amount) is 0.9 or more,
Further, the aging is characterized by having a chemical composition in which F1 ′ represented by the formula (1 ′) is 1.00 or less and F2 ′ represented by the formula (2 ′) is 0.30 or more. Hardenable steel.
F1 ′ = C + 0.1 × Si + 0.2 × Mn + 0.15 × Cr + 0.35 × V + 0.2 × Mo (1 ′)
F2 ′ = − 4.5 × C + Mn + Cr−3.5 × V−0.8 × Mo (2 ′)
The element symbols in the above formulas (1 ′) and (2 ′) mean the content of the element in mass%.

[3] The age-hardening steel according to [1] or [2], further containing one or more of Cu: 0.3% or less and Ni: 0.3% or less.

[4] The method according to any one of [1] to [3], further including at least one of Ca: 0.005% or less and Bi: 0.4% or less Age hardenable steel.

[5] After the age-hardening steel according to any one of [1] to [4] is heated at 1100 to 1350 ° C. for 0.1 to 300 minutes, the surface temperature after finish forging is 900 ° C. or higher. Forging, and then cooling to room temperature with an average cooling rate in the temperature range of 800 to 400 ° C. being 10 to 90 ° C./min, and
A cutting process for cutting the forged steel; and
An aging treatment step of holding the steel after cutting in a temperature range of 540 to 700 ° C. for 30 to 1000 minutes;
A method for producing a part using age-hardening steel, comprising:

  The age-hardening steel of the present invention has a hardness before aging treatment of 340 HV or less. In addition, the mechanical parts using the age-hardening steel of the present invention have a fatigue strength of 490 MPa or more due to the aging treatment performed after the cutting process. Further, the mechanical part has a toughness (absorbed energy at 20 ° C. after aging treatment evaluated by a Charpy impact test performed using a standard test piece with a U-notch having a notch depth of 2 mm and a notch bottom radius of 1 mm) of 25 J. That's it. Further, the mechanical part has a yield strength of 800 MPa or more. For this reason, the age-hardening steel of the present invention can be used very suitably as a material for machine parts such as automobiles, industrial machines, and construction machines.

It is a figure which shows the correlation with the steel material hardness before aging, and F1 value. It is a figure which shows the relationship between the steel material Charpy impact value after aging, and F2 value.

  Hereinafter, each requirement of the present invention will be described in detail. In addition, “%” of the content of each element means “mass%”.

<Age-hardening steel>
(Essential ingredients)
C: 0.09 to 0.20%
C is an important element in the present invention. C combines with V to form carbides and strengthens the steel. However, if the C content is less than 0.09%, V carbides are difficult to precipitate, and thus a desired strengthening effect cannot be obtained. On the other hand, if the C content is too high, the amount of C that does not bond to V or Mo forms Fe and carbide (cementite) increases, so that the toughness is deteriorated. Therefore, the content of C is set to 0.09 to 0.20%. The C content is preferably 0.10% or more, and more preferably 0.11% or more. The C content is preferably 0.18% or less, and more preferably 0.16% or less.

Si: 0.01-0.40%
Si is useful as a deoxidizing element at the time of steel making, and at the same time, has an action of improving the strength of the steel by dissolving in a matrix. In order to sufficiently obtain these effects, Si needs to be contained in an amount of 0.01% or more. However, in steel containing a large amount of Mn and Cr, if the Si content is excessive, the amount of retained austenite in the structure after hot forging becomes too large, and deformation during aging treatment may increase. Therefore, the Si content is set to 0.01 to 0.40%. The Si content is preferably 0.05% or more. Further, the Si content is preferably 0.35% or less, and more preferably 0.30% or less.

Mn: 1.5 to 2.5%
Mn has the effect of improving hardenability and making the structure bainite. Furthermore, by lowering the bainite transformation temperature, the bainite structure can be refined to increase the toughness of the matrix. Moreover, Mn has the effect | action which forms MnS in steel and improves the chip disposal property at the time of cutting. In order to obtain these effects sufficiently, the Mn content must be at least 1.5%. However, since Mn is an element that is easily segregated during solidification of steel, if the content is too large, it is inevitable that the variation in hardness in the part after hot forging becomes large. Therefore, the Mn content is set to 1.5 to 2.5%. The Mn content is preferably 1.6% or more, and more preferably 1.7% or more. Further, the Mn content is preferably 2.3% or less, and more preferably 2.1% or less.

S: 0.001 to 0.045%
Since S combines with Mn in steel to form MnS and improves chip disposability during cutting, it is necessary to contain 0.001% or more. However, when the S content increases, coarse MnS increases and deteriorates toughness and fatigue strength. In particular, when the S content exceeds 0.045%, the toughness and fatigue strength decrease remarkably. Therefore, the content of S is set to 0.001 to 0.045%. The S content is preferably 0.005% or more, and more preferably 0.010% or more. Further, the S content is preferably 0.040% or less, and more preferably 0.035% or less.

Cr: More than 1.00% and 2.00% or less Cr, like Mn, has an effect of improving hardenability and making the structure bainite. Furthermore, the bainite structure is refined by lowering the bainite transformation temperature. Furthermore, the mobility of the grain boundary is lowered, the austenite grain size at the time of hot forging is refined, and as a result, the bainite structure after transformation is refined. Cr has the effect of increasing the toughness of the base material through the effect of refining these bainite structures. In order to obtain these effects sufficiently, it is necessary to contain more than 1.00%. However, if the Cr content exceeds 2.0%, the hardenability increases and the hardness before aging treatment may exceed 340 HV. Therefore, the Cr content is set to exceed Cr: 1.00% and not more than 2.00%. The Cr content is preferably 1.10% or more. The Cr content is preferably 1.80% or less, and more preferably 1.60% or less.

Al: 0.001 to 0.060%
Al is an element having a deoxidizing action, and in order to obtain this effect, the content needs to be 0.001% or more. However, when Al is contained excessively, a coarse oxide is generated, and the toughness is lowered. Therefore, the content of Al is set to 0.001 to 0.060%. The Al content is preferably 0.050% or less.

V: 0.22-0.55%
V is the most important element in the steel of the present invention. V combines with C during the aging treatment to form fine carbides, thereby increasing the fatigue strength. In addition, when Mo is contained in the steel, V has an effect of further aging hardening ability by being combined with Mo and precipitated by aging treatment. In order to obtain these effects sufficiently, V needs to be 0.22% or more. However, if the V content is excessive, undissolved carbonitrides are likely to remain even during heating during hot forging, leading to a decrease in toughness. Moreover, if the V content is excessive, the hardness before aging treatment may increase. Therefore, the content of V is set to 0.22 to 0.55%. The V content is preferably less than 0.45%, and more preferably 0.40% or less. Further, the V content is preferably 0.25% or more, and more preferably 0.27% or more.

N: more than 0.0080 and 0.0170% or less N has the effect of promoting the precipitation of V carbonitride during aging and increasing the yield strength. In order to sufficiently obtain this effect, the N content needs to be more than 0.0080%. However, if the N content exceeds 0.0170%, the V carbonitride does not form a solution during hot forging, and it becomes difficult to precipitate a sufficient amount of fine V carbonitride during subsequent aging. Therefore, the yield strength decreases. Therefore, the N content is set to more than 0.0080 and 0.0170% or less. The N content is preferably 0.0090% or more, and more preferably 0.0100% or more. The N content is preferably 0.0160% or less, and more preferably 0.0150% or less.

  The age-hardenable steel of the present invention comprises the above-described elements from C to N, the balance Fe and impurities, and P and Ti in the impurities are P: 0.03% or less and Ti: 0.005% The area ratio of the bainite structure is 80% or more, and the effective V ratio (V solid solution amount / V total amount) is 0.9 or more.

(impurities)
An impurity refers to what is mixed from ore as a raw material, scrap, a manufacturing environment, etc. when manufacturing steel materials industrially.

P: 0.03% or less P is an element which is contained as an impurity and is not preferable in the present invention. That is, P reduces toughness by segregating at the grain boundaries. Therefore, the content of P is set to 0.03% or less. The P content is preferably 0.025% or less.

Ti: Less than 0.005% Ti is contained as an impurity and is an element that is not particularly preferable in the present invention. That is, Ti combines with N and / or C to form TiN and / or TiC, leading to a decrease in toughness. In particular, when the content is 0.005% or more, the toughness is greatly deteriorated. Therefore, the Ti content is less than 0.005%. In order to ensure good toughness, the Ti content is preferably 0.0035% or less.

(Organization)
In the age-hardenable steel of the present invention, the area ratio of the bainite structure is 80% or more. Here, the area ratio of the bainite structure means an area ratio when the metal structure at a position from the depth of 1/3 to 1/2 of the thickness from the surface of the steel material is observed with an optical microscope. If the area ratio of the bainite structure is 80% or more, precipitation of V is suppressed, the effective V ratio is increased, and high fatigue strength and 0.2% yield strength can be obtained.

(Effective V ratio)
The effective V ratio (V solid solution amount / V total amount) is 0.9 or more. Here, the effective V ratio means the amount of solid solution in the total amount of V contained in the steel. If the effective V ratio is 0.9 or more, the amount of V carbonitride precipitated by aging treatment increases, and high fatigue strength and 0.2% yield strength can be obtained.

(Optional ingredient)
Reference will now be made to optional ingredients that may be included in the age hardenable steel of the present invention.

Mo: 0.9% or less Mo, like V, has a relatively low carbide precipitation temperature and is an element suitable for age hardening. Mo enhances hardenability, has the effect of increasing the area ratio while making the structure after hot forging bainite. Mo has a function of increasing age-hardening ability by forming carbides in combination with V in steel containing 0.22% or more of V. For this reason, you may contain Mo as needed. However, since Mo is a very expensive element, when the content increases, the manufacturing cost of steel increases and the toughness also decreases. Therefore, the Mo content in the case of inclusion is set to 0.9% or less. When Mo is contained, the amount of Mo is preferably 0.75% or less, more preferably 0.60% or less, and even more preferably less than 0.50%. On the other hand, in order to stably obtain the effect of Mo described above, the amount of Mo in the case of inclusion is desirably 0.05% or more, and more desirably 0.10% or more.

Cu: 0.3% or less Cu has an effect of improving fatigue strength. For this reason, you may contain Cu as needed. However, when the Cu content increases, hot workability decreases. Therefore, the amount of Cu in the case of inclusion is set to 0.3% or less. When Cu is contained, the amount of Cu is preferably 0.25% or less. On the other hand, in order to stably obtain the effect of increasing the fatigue strength of Cu, the amount of Cu in the case of inclusion is preferably 0.1% or more.

Ni: 0.3% or less Ni has an effect of improving fatigue strength. Furthermore, Ni also has the effect | action which suppresses the fall of the hot workability by Cu. For this reason, you may contain Ni as needed. However, when the content of Ni increases, the above effect is saturated in addition to the increase in cost. Therefore, the amount of Ni in the case of inclusion is set to 0.3% or less. When Ni is contained, the amount of Ni is preferably 0.25% or less. On the other hand, in order to stably obtain the effect of Ni described above, the amount of Ni in the case of inclusion is preferably 0.1% or more.

  Said Cu and Ni can be contained only in any 1 type or 2 types of composites. The total content of the above elements in the case of inclusion can be 0.6% in the case where the contents of Cu and Ni are the respective upper limit values.

Ca: 0.005% or less Ca has an action of extending the tool life. For this reason, you may contain Ca as needed. However, when the content of Ca increases, a coarse oxide is formed and the toughness is deteriorated. Therefore, the Ca content in the case of inclusion is set to 0.005% or less. When Ca is contained, the amount of Ca is preferably 0.0035% or less. On the other hand, in order to stably obtain the effect of extending the life of the above-mentioned Ca tool, the Ca content in the case of inclusion is preferably 0.0005% or more.

Bi: 0.4% or less Bi has the effect of reducing the cutting resistance and extending the tool life. For this reason, you may contain Bi as needed. However, when the Bi content is increased, the hot workability is lowered. Therefore, the amount of Bi when contained is set to 0.4% or less. When Bi is contained, the amount of Bi is preferably 0.3% or less. On the other hand, in order to stably obtain the effect of extending the life of the Bi tool, the amount of Bi in the case of inclusion is preferably 0.03% or more.

  Said Ca and Bi can be contained only in any 1 type in them, or 2 types of composites. The total content of these elements in the case of inclusion may be 0.405% in the case where the Ca and Bi contents are the respective upper limit values, but is preferably 0.3% or less. .

(Values calculated by mathematical formulas using specific element content: F1 (F1 ′), F2 (F2 ′))
Matters of the present invention Hardening steel satisfies the above-mentioned conditions regarding chemical composition (essential and optional components), structure, and effective V ratio, and further is a value calculated by a mathematical formula using the content of a specific element. F1 (F1 ′) and F2 (F2 ′) are 1.00 or less and 0.30 or more, respectively.

First, the value F1 (F1 ′) calculated by a mathematical formula using the content of a specific element will be described.
That is, when the optional element from Mo to Bi is not included,
F1 = C + 0.1 × Si + 0.2 × Mn + 0.15 × Cr + 0.35 × V (1)
F1 represented by
When containing one or more optional elements from Mo to Bi,
F1 ′ = C + 0.1 × Si + 0.2 × Mn + 0.15 × Cr + 0.35 × V + 0.2 × Mo (1 ′)
F1 ′ represented by
Each is 1.00 or less.

  In addition, the element symbol in said (1) Formula and (1 ') Formula means content in the mass% of the element.

  F1 and F1 'are indices indicating the hardness before aging treatment. If the age-hardenable steel of the present invention satisfies the above-mentioned conditions regarding F1 or F1 ′, the hardness before aging treatment does not become too high, the cutting resistance at the time of cutting does not increase, and the tool life is increased. Is also realized.

  F1 and F1 'are preferably 0.97 or less, and more preferably 0.95 or less. Further, F1 and F1 'are preferably 0.60 or more, and more preferably 0.65 or more.

  FIG. 1 is a graph showing the relationship between pre-aging hardness (vertical axis; HV) and F1 values (horizontal axis) of various steel types. As is clear from the graph of FIG. 1, a strong first-order positive correlation is recognized between the two, and if F1 ≦ 1.00 or less, the pre-aging hardness ≦ 340 HV is satisfied. I understand.

Next, the value F2 (F2 ′) calculated by a mathematical formula using the content of a specific element will be described.
That is, in the case where any element from Mo to Bi is not included,
F2 = −4.5 × C + Mn + Cr−3.5 × V (2)
F2 represented by
When containing one or more optional elements from Mo to Bi,
F2 ′ = − 4.5 × C + Mn + Cr−3.5 × V−0.8 × Mo (2 ′)
F2 ′ represented by
Each is 0.30 or more.

  In addition, the element symbol in said (2) Formula and (2 ') Formula means content in the mass% of the element.

  F2 and F2 'are indices indicating toughness after aging treatment. That is, if the condition of F1 or F1 'is satisfied, the toughness after the aging treatment may be lowered and the target toughness may not be ensured. Therefore, it is necessary to separately define F2 and F2'.

  FIG. 2 is a diagram showing the relationship between the steel Charpy impact value after aging and the F2 value. As shown in the figure, there is also a positive correlation between the Charpy impact value (J) after aging treatment and the F2 value (horizontal axis), and when F2 or F2 ′ is less than 0.30, The toughness after the aging treatment cannot be obtained sufficiently. In order to ensure the target toughness while obtaining a yield strength of 800 MPa or more, the content of each alloy element is within the specified range, and F1 or F1 ′ is satisfied. Alternatively, it is necessary to satisfy the condition of F2 ′.

  F2 and F2 'are preferably 0.45 or more, and more preferably 0.60 or more.

  In addition, when F2 becomes large, the hardness before aging often becomes large. However, as long as F1 is controlled to 1.00 or less, even if F2 is large, the hardness before aging becomes too large and machinability does not deteriorate. Therefore, there is no need to particularly limit the upper limit of F2. Similarly, if F1 'is 1.00 or less, there is no need to particularly limit the upper limit of F2'.

<Method for producing age-hardening steel>
The method for producing the age-hardening steel of the present invention is not particularly limited, and the chemical composition may be adjusted by melting by a general method.

<Manufacturing method of parts using age-hardening steel>
Below, an example of the method of manufacturing machine parts, such as a motor vehicle, an industrial machine, a construction machine, is shown using the age hardening steel of the present invention manufactured as mentioned above as a raw material.

  First, a material subjected to hot forging (hereinafter referred to as “hot forging material”) is produced from steel whose chemical composition is adjusted to the above-described range. As the material for hot forging, billets obtained by performing ingot rolling on ingots, billets obtained by performing ingot rolling on continuous cast materials, or steel bars obtained by hot rolling or hot forging these billets can be used.

  Next, the above hot forging material is hot forged and further cut to finish the workpiece into a predetermined part shape. The hot forging is performed, for example, by heating the hot forging material at 1100 to 1350 ° C. for 0.1 to 300 minutes, and then the surface temperature after finish forging becomes 900 ° C. or higher, and then 800 It cools to room temperature by making the average cooling rate of the temperature range to -400 degreeC into 10-90 degreeC / min.

  Further, the workpiece cooled as described above is further cut to finish a predetermined part shape.

  Finally, the workpiece is subjected to an aging treatment to obtain machine parts such as automobiles, industrial machines, and construction machines having desired characteristics. The aging treatment is performed, for example, in a temperature range of 540 to 700 ° C, preferably in a temperature range of 560 to 680 ° C. The retention time of this aging treatment is adjusted by the size (mass) of the machine part for soaking, but can be 30 to 1000 minutes.

  Steels 1-27 having chemical compositions shown in Table 1 were melted in a 50 kg vacuum melting furnace. Steels 1 to 17 in Table 1 are steels whose chemical compositions are within the range defined by the present invention. On the other hand, steels 18 to 27 in Table 1 are steels whose chemical compositions deviate from the conditions specified in the present invention.

  Each steel type ingot was heated at 1250 ° C. and then hot forged into a steel bar having a diameter of 60 mm. Each hot forged steel bar was once allowed to cool in the atmosphere and cooled to room temperature. Then, it heated at 1250 degreeC for 30 minutes, the forging to a component shape was assumed, the surface temperature of the forging material at the time of finishing was 950-1100 degreeC, and it hot-forged to the steel bar of diameter 35mm. After hot forging, all were allowed to cool in air and cooled to room temperature. The cooling rate when allowed to cool in the atmosphere is that of hot forging again by embedding a thermocouple in the vicinity of R / 2 of the steel bar hot-forged under the above conditions ("R" represents the radius of the steel bar). The temperature was raised to a temperature close to the finishing temperature and then allowed to cool in the air for measurement. The average cooling rate in the temperature range from 800 to 400 ° C. after forging measured in this way was about 40 ° C./min.

  For each steel type, a part of the steel bar cooled to room temperature after finishing to a diameter of 35 mm by hot forging is cut off by 100 mm at both ends of the steel bar without being subjected to an aging treatment (that is, in a cooled state). After that, a test piece was cut out from the remaining central portion, and the hardness before aging treatment was investigated.

  On the other hand, for each steel type, the hot-forged steel bar was subjected to aging treatment at 600 to 630 ° C. for 60 to 180 minutes. After cutting off both ends of the steel bar by 100 mm, the test piece was cut out from the remaining central part. The hardness after aging treatment was investigated. Moreover, about each steel type, the test piece was cut out from the bar steel, and the absorbed energy, fatigue strength, and yield strength in the Charpy impact test after the aging treatment were investigated.

  Hardness measurement was performed as follows. First, a test piece was prepared by crossing a steel bar, filling the resin so that the cut surface became the test surface, and mirror polishing. Next, in accordance with “Vickers hardness test—test method” in JIS Z 2244 (2009), the test force is set to 9 for 10 points near the R / 2 part (“R” represents a radius) of the test surface. The hardness was measured as 8N. The above 10 points were arithmetically averaged to obtain Vickers hardness. When the hardness before aging treatment was 340 HV or less, it was judged that even parts that were machined under various conditions could be industrially mass-produced, and this was the target. When the specimens after the hardness measurement were corroded with the nital and the structure was observed, the specimens of all steel types were mainly bainite and some MA structures were mixed.

  The toughness after the aging treatment is evaluated by a Charpy impact test conducted using a standard test piece with a U-notch having a notch depth of 2 mm and a notch bottom radius of 1 mm, and the absorbed energy at a test temperature of 20 ° C. is 25 J or more. Judged that it was high enough, and aimed this.

The fatigue strength was investigated by preparing an Ono-type rotating bending fatigue test piece having a parallel part diameter of 8 mm and a length of 106 mm. That is, the above-mentioned test piece is collected so that the center of the fatigue test piece is R / 2 part of the steel bar, the number of tests is 8, and the Ono type rotation is performed at room temperature and in the atmosphere under the condition that the stress ratio is -1. A bending fatigue test was performed. The maximum value of the stress amplitude when the number of repetitions was not broken up to 1.0 × 10 ⁷ times was defined as the fatigue strength. When the fatigue strength was 490 MPa or more, it was judged that the fatigue strength was sufficiently high, and this was the target.

  Tensile test using a JIS No. 14A tensile test piece with a parallel part of φ6 is performed, 0.2% proof stress is obtained by the offset method with the specified plastic strain amount being 0.2%, and the yield strength is Equal to. When the yield strength was 800 MPa or more, it was judged to be sufficiently high, and this was the target. Table 2 shows the results of the above investigations.

  As is apparent from Table 2, the chemical composition, structure, and effective V ratio (V solid solution amount / V total amount) specified by the present invention, and a value calculated by a mathematical formula using the content of a specific element, In the case of the “examples of the present invention” of the test numbers A1 to A17 having, the hardness before aging treatment is 340 HV or less, the hardness by the aging treatment is fatigue strength of 510 MPa or more, the yield strength is 815 MPa or more, and the absorbed energy in the Charpy impact test Is over 36J. For this reason, since both achieved the target value, both strength and toughness after aging treatment are compatible, and the hardness before aging treatment is also low, so the cutting resistance is reduced and the tool life is extended. You can see what you can expect.

On the other hand, in the case of “Comparative Examples” with test numbers B1 to B10 that are out of the definition of the present invention, at least one of the target performances is not obtained.

  The age-hardening steel of the present invention can ensure a suitable hardness before aging treatment (340 HV or less), and it can be expected that the cutting resistance is lowered and the tool life is extended. Moreover, if the age-hardening steel of the present invention is used, a suitable fatigue strength (490 MPa or more), yield strength (800 MPa or more), and impact value (25 J or more) are also obtained by an aging treatment performed after cutting. Can be secured. For this reason, the age-hardening steel of the present invention can be used very suitably as a material for machine parts such as automobiles, industrial machines, and construction machines.

Claims (5)

In mass%, C: 0.09 to 0.20%, Si: 0.01 to 0.40%, Mn: 1.5 to 2.5%, S: 0.001 to 0.045%, Cr: 1.00% to 2.00% or less, Al: 0.001 to 0.060%, V: 0.22 to 0.55%, and N: 0.0080 to 0.0170% or less The balance consists of Fe and impurities, and P and Ti in the impurities are P: 0.03% or less and Ti: less than 0.005%,
The area ratio of the bainite structure is 80% or more,
The effective V ratio (V solid solution amount / V total amount) is 0.9 or more,
Furthermore, the age-hardenable steel has a chemical composition in which F1 represented by the following formula (1) is 1.00 or less and F2 represented by the formula (2) is 0.30 or more.
F1 = C + 0.1 × Si + 0.2 × Mn + 0.15 × Cr + 0.35 × V (1)
F2 = −4.5 × C + Mn + Cr−3.5 × V (2)
The element symbols in the above formulas (1) and (2) mean the content in mass% of the element.
In mass%, C: 0.09 to 0.20%, Si: 0.01 to 0.40%, Mn: 1.5 to 2.5%, S: 0.001 to 0.045%, Cr: More than 1.00% and 2.00% or less, Al: 0.001 to 0.060%, V: 0.22 to 0.55%, Mo: 0.9% or less, and N: 0.0080 More than 0.0170% and the balance consists of Fe and impurities, P and Ti in the impurities are P: 0.03% or less and Ti: less than 0.005%,
The area ratio of the bainite structure is 80% or more,
The effective V ratio (V solid solution amount / V total amount) is 0.9 or more,
Further, the aging is characterized by having a chemical composition in which F1 ′ represented by the formula (1 ′) is 1.00 or less and F2 ′ represented by the formula (2 ′) is 0.30 or more. Hardenable steel.
F1 ′ = C + 0.1 × Si + 0.2 × Mn + 0.15 × Cr + 0.35 × V + 0.2 × Mo (1 ′)
F2 ′ = − 4.5 × C + Mn + Cr−3.5 × V−0.8 × Mo (2 ′)
The element symbols in the above formulas (1 ′) and (2 ′) mean the content of the element in mass%.   The age-hardenable steel according to claim 1 or 2, further comprising at least one of Cu: 0.3% or less and Ni: 0.3% or less.   The age-hardenable steel according to any one of claims 1 to 3, further comprising at least one of Ca: 0.005% or less and Bi: 0.4% or less. The age-hardening steel according to any one of claims 1 to 4 is heated at 1100 to 1350 ° C for 0.1 to 300 minutes, and then forged so that the surface temperature after finish forging becomes 900 ° C or higher. Performing a forging step of cooling to room temperature at an average cooling rate of 10 to 90 ° C./min in the temperature region from 800 to 400 ° C.,
A cutting process for cutting the forged steel; and
An aging treatment step of holding the steel after cutting in a temperature range of 540 to 700 ° C. for 30 to 1000 minutes;
A method for producing a part using age-hardening steel, comprising:

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