JP2009132949A - Steel material with excellent cold workability, and cold worked parts - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a steel material for cold working, which exhibits excellent cold workability during working and secures superior strength of parts after cold working and accordingly can satisfy the life of forming dies and further has practicality in energy saving. <P>SOLUTION: The steel material has a composition which consists of, by mass, 0.06 to 0.5% C, 0.01 to 0.1% Si, 0.2 to 1.5% Mn, ≤0.05% (not including 0%) P, ≤0.05% (not including 0%) S, ≤0.6% (not including 0%) Sn, ≤0.04% (not including 0%) N and the balance Fe with inevitable impurities and in which the content of solid-solution N (Sol.N) is ≥0.006% and satisfies inequality (1) 10≤Sn/Sol.N≤40. <P>COPYRIGHT: (C)2009,JPO&INPIT

Description

  The present invention relates to a steel material for cold working useful as a raw material for manufacturing machine parts such as bolts and nuts, in particular, various parts for automobiles, in particular, a wire rod for cold working and a bar steel. Furthermore, the present invention also relates to a cold-worked part produced from the cold-working steel, and further to a method for producing a cold-worked steel material by heat treatment or thermomechanical treatment.

  In recent years, from the viewpoint of environmental protection, there is an increasing demand for weight reduction of parts intended to improve the fuel efficiency of vehicles such as automobiles. General high-strength parts that can withstand this type of weight reduction ensure the required strength of the parts by increasing the content of various alloy elements added to the base metal.

  Moreover, the optimal processing method applied to this seed steel is usually cold processing in an atmosphere of 200 ° C. or less, and this cold processing has higher productivity than hot processing and warm processing. In addition, both dimensional accuracy and steel yield are advantageous.

  By the way, when manufacturing parts by such cold working, the problem is that in order to ensure the strength of the cold-worked parts to be higher than the expected value, the deformation resistance is inevitably required. Therefore, it is necessary to use a steel material having a high height. However, the higher the deformation resistance of the steel material used, there is not only a reduction in the service life of the cold working mold, but also there is a difficulty that cracks are likely to occur during cold working.

  Considering this point, a method of manufacturing a high-strength part having a predetermined strength (hardness) by performing a heat treatment such as quenching and tempering after cold working a steel material into a predetermined shape is conventionally performed. There was also. However, since the heat treatment after cold working inevitably changes if the part dimensions are small, it is necessary to correct by secondary machining such as cutting, and there is a solution that can omit heat treatment and subsequent machining. It is desired.

  In order to improve the situation as described above, several measures have already been taken to reduce the deformation resistance of steel during cold working, and at the same time, to ensure the specified component strength, and to improve productivity and save energy. Proposed.

  The following Patent Document 1 discloses that cold workability that can be used in a rolling state is usually because the softening-purpose spherical annealing that is performed before cold working requires heating for a long time and there is a problem in terms of energy consumption. We propose a method for producing wire rod-like steel with good quality. That is, fine nitrides are precipitated in ferrite grains, and a C compound such as cementite is precipitated as a nucleus, thereby suppressing an increase in deformation resistance during cold working at 100 to 350 ° C.

  Further, Patent Document 2 discloses a steel bar wire having excellent strain aging resistance in consideration of a decrease in tool life due to dynamic strain aging and product embrittlement when cold forging the seed steel bar at 100 to 200 ° C. Disclose the manufacturing method. That is, by controlling the amount of N and solute Al in the steel material to fix N as AlN, and further precipitating C as a C compound by age hardening at 200 to 500 ° C., It is said that age hardening due to dissolved N is suppressed.

  In both methods of Patent Documents 1 and 2, in order to suppress an increase in deformation resistance due to dynamic strain aging, solid solution N and solid solution C existing in ferrite grains are respectively fixed as an N compound and a C compound. It is. Therefore, in order to fix the solid solution N, it is necessary to add Al which is an N compound forming element. However, as shown in the examples of the invention, if the amount of Al added is about 0.039 to 0.045%, even if the amount of N in the steel is 0.015%, solute N Most of them are fixed as N compounds by Al, so it is considered that almost no solid solution N exists. A part produced by processing such a steel material has a part strength corresponding to the deformation resistance during the processing.

  Patent Document 3 below discloses a low C steel bar wire for cold heading for the purpose of reducing deformation resistance of steel by high speed forging at 200 to 400 ° C. and improving tool life. This steel material is based on Al killed steel, and Cr is added to this, which has a solid solution softening action. Furthermore, by fixing solid solution N by further adding Al, deformation resistance during cold working is reduced. . However, in this method, since solid solution N is immobilized as an N compound by adding Al, it is assumed that there is almost no solid solution N as in Patent Documents 1 and 2.

  As described above, this type of steel part material has properties that are contradictory to cold workability, that is, deformation resistance and deformability, and part strength after cold working. Therefore, when it is attempted to secure a predetermined component strength, common problems such as a deterioration of the mold life and a tendency to crack during processing occur. On the other hand, if the cold workability is improved in order to improve the die life, a predetermined component strength cannot be secured.

  From such a situation, the conventional techniques as represented by the above examples still have insufficiency to produce a non-tempered cold-working steel with good properties of both. .

Further, as described above, this kind of cold-worked steel part may be subjected to hardening heat treatment such as quenching and tempering in order to ensure a predetermined part strength. Therefore, it is required to omit the heat treatment for quenching and tempering.
JP 2000-008139 A Japanese Patent Laid-Open No. 60-082618 Japanese Patent Publication No.57-060416

  The present invention exhibits excellent cold workability during the processing, and after the cold processing, the strength as a good component product is ensured, and therefore the life of the molding die can be satisfied. The main issue is to provide practical steel materials for cold work in terms of energy saving. Moreover, this invention makes it a subject to provide the components for cold work made from the same wire and steel bar.

In order to solve the above-mentioned problems, the present invention provides a steel material for cold working characterized by the inclusion of Sn and N and the control of solute N by the following means, and cold working by heat treatment / work heat treatment of this steel. It is characterized by a method for manufacturing steel materials and high-quality product parts obtained by cold working of the steel materials.
(1) C: 0.06 to 0.5% (mass%, the same shall apply hereinafter), Si: 0.01 to 0.1%, Mn: 0.2 to 1.5%, P: 0.05% Or less (excluding 0%), S: 0.05% or less (not including 0%), Sn: 0.6% or less (not including 0%), N: 0.04% or less ( The balance is composed of Fe and inevitable impurities, the content of solid solution N (Sol. N) is 0.006% or more, and the quantitative ratio of Sn to solid solution N is A steel material excellent in cold workability characterized by satisfying the following formula (1).

10 ≦ Sn / Sol. N ≦ 40 (1)
(2) A steel material excellent in cold workability as described in (1) above, containing N: 0.007% or more.
(3) Al: 0.2% or less (not including 0%), Zr: 0.2% or less (not including 0%), Ti: 0.2% or less (not including 0%) Nb: 0.5% or less (not including 0%), V: 0.5% or less (not including 0%), Ta: 0.1% or less (not including 0%), Hf : 0.1% or less (excluding 0%) and B: 0.002% or less (not including 0%), containing one or two or more selective elements selected from the group consisting of N The steel material having excellent cold workability as described in the above item (1) or (2), wherein the quantitative relationship between the element and the selected element satisfies the following formula (2):

N (%)-{14 * Al (%) / 27 + 14 * Ti (%) / 47.9
+ 14 * Nb (%) / 92.9 + 14 * V (%) / 50.9
+ 14 * Zr (%) / 91.2 + 14 * B (%) / 100.8
+ 14 * Ta (%) / 180.9 + 14 * Hf (%) / 178.5}
≧ 0.006% (2)
However, * in a formula represents a product.
(4) A steel material excellent in cold workability according to any one of the above (1) to (3), which contains Cr: 2% or less (excluding 0%).
(5) The steel material having excellent cold workability according to any one of the above (1) to (4), which contains Cu: 5% or less (excluding 0%).
(6) Ni: 5% or less (not including 0%) and / or Co: 5% or less (not including 0%), any one of (1) to (5) above Steel with excellent cold workability.
(7) Cold working as described in the above items (1) to (6), which contains Mo: 2% or less (not including 0%) and / or W: 2% or less (not including 0%) Excellent steel material.
(8) Ca: 0.05% or less (not including 0%), REM: 0.05% or less (not including 0%), Mg: 0.02% or less (not including 0%) Li: 0.02% or less (excluding 0%), Pb: 0.3% or less (not including 0%), Bi: 0.2% or less (not including 0%) A steel material excellent in cold workability according to any one of the above items (1) to (7), comprising one or more selected from the group.
(9) A cold-worked part obtained by cold-working the steel material according to any one of (1) to (8) above at a working temperature of 200 ° C or lower.
(10) The cold worked component as described in (9) above, wherein the component strength satisfies the relationship of the following expression (3) with respect to the deformation resistance during cold working.

H ≧ (DR + 1000) / 6 (3)
H: Strength of parts after cold working (Hv)
DR: Deformation resistance during cold working (MPa)

  Since the steel for cold working of the present invention contains an amount of solute N that is larger than the normal predetermined amount, even if the heat treatment for quenching and tempering after the cold working is omitted, the cold working steel has a predetermined amount after the cold working. Part strength can be ensured. Further, the steel for cold working of the present invention is added with Sn, the ratio of the content of Sn and N is optimized in a certain range, and the use is cold at about 200 ° C. or less. Since it is oriented to machining, good cold workability can be expected with certainty. At the same time, there is an advantage that the life of the molding die to be used is unnecessarily hindered by the workpiece, which is effectively relieved.

  First, the chemical composition of the steel material excellent in cold workability of the present invention will be described.

  In the steel material according to the present invention, as basic components, C: 0.06 to 0.5%, Si: 0.01 to 0.1%, Mn: 0.2 to 1.5%, P: 0.05 % Or less (excluding 0%) and S: 0.05% or less (excluding 0%). Further, it is characterized by containing Sn: 0.6% or less (not including 0%) and N: 0.04% or less (not including 0%). And the content (Sol.N) of N as a solid solution state is 0.006% or more, and at the same time, the quantitative ratio of Sn to the solid solution N is adjusted so as to satisfy the following formula (1). It is characterized by.

10 ≦ Sn / Sol. N ≦ 40 (1)
The role of each component and the reason for limiting the content will be described in detail below.
・ C: 0.06-0.5%
C is a deoxidizing element and needs to be contained in an amount of 0.06% or more. If it is less than that, a gas is generated during the solidification process, resulting in defects such as deterioration of deformability. A more preferred lower limit is 0.07%. However, when the amount of C is excessive, it causes deterioration of cold workability due to an increase in deformation resistance and deterioration of machinability due to an increase in C compound, so the upper limit is made 0.5%, preferably 0.45%. It is.
・ Si: 0.01-0.1%
Si is an element used as a deoxidizer in the steelmaking process. If the content is small, gas is generated during the solidification process due to insufficient deoxidation, and defects such as deterioration of deformability occur. It is necessary to add, and a preferable lower limit is 0.02%. However, excessive addition causes cracking and increased deformation resistance, so the upper limit is made 0.1%, and the preferred upper limit is 0.09%.
・ Mn: 0.2-1.5%
Mn is a deoxidation / desulfurization element in the steelmaking process. If the content is small, FeS precipitates in the form of a film at the crystal grain boundary, which significantly reduces the grain boundary strength and deteriorates the deformability. It is necessary to add. A more preferred lower limit is 0.3%. However, excessive addition causes an increase in deformation resistance and deteriorates cold workability, so the upper limit is made 1.5%. A preferable upper limit is 1.2%.
P: 0.05% or less (excluding 0%)
P is an inevitable impurity element, but when it is contained in ferrite, it segregates at the ferrite grain boundaries and deteriorates the cold workability, while the ferrite is solid-solution strengthened to increase the deformation resistance. Therefore, it is desirable to reduce P as much as possible from the viewpoint of cold workability. However, since extreme reduction leads to an increase in steelmaking cost, the upper limit is made 0.05% in consideration of process capability. Preferably, it is 0.03% or less, but it is industrially difficult to make it completely zero.
S: 0.05% or less (excluding 0%)
S is also an inevitable impurity element, but this content forms inclusions of MnS and degrades cold workability, so it is desirable to reduce it as much as possible, and the upper limit is made 0.05% from the viewpoint of deformability, Preferably it is 0.03% or less. However, on the other hand, S is an element effective for improving the machinability, and extreme reduction deteriorates the machinability. Therefore, considering machinability, it is preferably 0.002% or more, more preferably 0. It is good to make it contain 0.006% or more.
Sn: 0.6% or less (excluding 0%)
Sn is an active additive element that is most important in the present invention, and is effective in suppressing an increase in deformation resistance of a steel material due to solute N during cold working. However, Sn segregates at the ferrite grain boundaries and promotes embrittlement during continuous casting of the material steel, so avoid excessive addition and set the upper limit to 0.6%, more preferably 0.55% or less. Note that the lower limit of the Sn amount needs to be added in an amount of 0.06% or more in order to satisfy the condition of the formula (1) described below, preferably 0.1% or more, from the relationship with the solute N amount. And

Sn can contribute to energy saving because scrap material can be used effectively.
N: 0.04% or less (excluding 0%)
N has the effect of improving the strength of the steel part after cold working by dissolving in the steel, and in the present invention, N is an important element contained together with the above Sn. However, if the total amount of N in steel is excessive, the amount of solute N will also be excessive, which may cause cracks during cold working of steel materials, and also cause internal defects in steel materials and slab cracks during continuous casting. It becomes easy to do. Therefore, from the viewpoint of steel deformability, material stability, and yield improvement during continuous casting, the upper limit of the total N content in the steel is 0.04%, more preferably 0.03% or less.

On the other hand, in order to satisfy the lower limit of the solute N amount described below, the total N amount is preferably secured as 0.007% or more as a steel material. That is, below this, it becomes difficult to secure a sufficient amount of solute N, and the deformation resistance of the material must be increased in order to obtain a predetermined component strength. Therefore, the total N amount is preferably 0.0075% or more, preferably 0.008% or more.
-Solid solution N amount: 0.006% or more Solid solution N (Sol. N) has the effect of improving the component strength after cold working as described above, and in order to ensure the desired component strength, A major feature of the present invention is that it contains 0.006% or more. The amount of solute N is preferably 0.007% or more, more preferably 0.008% or more. However, when the amount of solute N is excessive, cold workability is deteriorated, so the content is preferably 0.03% or less. In addition, naturally the upper limit of the amount of solute N does not exceed 0.04% which is the upper limit of the total N amount in steel.

  Thus, the present invention improves the strength of parts after cold working by containing a predetermined amount or more of solute N, and by controlling the quantitative ratio of Sn and N to a specific range, This is an unprecedented idea of maintaining good cold workability by suppressing the adverse effect of the amount of dissolved N during cold work. This point will be described later.

  In addition, the value of the “solid solution N amount” in the present invention is calculated by subtracting all N compounds from the total N amount in steel according to JIS G 1228. A practical measurement method is illustrated below.

(A) Inert gas melting method-thermal conductivity method A sample is cut out from the test steel material, placed in a crucible, melted in an inert gas stream, extracted N, transported to a thermal conductivity cell and heated. Measure the change in conductivity.

(B) Ammonia distillation separated indophenol blue spectrophotometric method This method consists of melting a sample cut from a test steel material in a 10% AA-based electrolyte and conducting constant-current electrolysis to obtain the total amount of N compounds in the steel. Is to measure. This electrolytic solution is a non-aqueous solvent type electrolytic solution composed of 10% acetylacetone, 10% tetramethylammonium chloride, and the balance: methanol, and does not generate a passive film on the steel surface.

  About 0.5 g of a sample of the test steel material is dissolved in the electrolytic solution, and the insoluble residue (N compound) is filtered through a polycarbonate filter having a hole size of 0.1 μm. The insoluble residue is decomposed by heating in a chip made of sulfuric acid, potassium sulfate and pure copper, and combined with the filtrate. After making this solution alkaline with sodium hydroxide, steam distillation is performed, and the distilled ammonia is absorbed by dilute sulfuric acid. Phenol, sodium hypochlorite and sodium pentacyanonitrosyl iron (III) are added to form a blue complex, and its absorbance is measured using a photometer.

By subtracting the total N compound amount (b) from the total N amount (a) in the steel determined by this method, the solid solution N amount in the steel is calculated.
・ 10 ≦ Sn / Sol. N ≦ 40 (1)
In the present invention, for the purpose of quantitatively prescribing the proportion of Sn required to suppress an increase in deformation resistance of steel due to solute N in steel, a large number of the above basic steel components are presupposed. It is the feature to use this formula that is derived from the aggregation of the experimental results.

  That is, Sn / Sol. When the N ratio is 10 or less, Sn cannot sufficiently suppress an increase in deformation resistance due to solute N, leading to an increase in deformation resistance and a decrease in workability. Preferred is 12 ≦ Sn / Sol. N, more preferably 15 ≦ Sn / Sol. N.

  In addition, Sn / Sol. Even if the N ratio is 40 or more, not only the effect of Sn is saturated but also the deformation resistance is increased by the solid solution N strengthening action of Sn. N ≦ 38, more preferably Sn / Sol. N ≦ 35.

  The basic composition of the steel of the present invention is as described above, and the balance is substantially iron, and it is naturally allowed that the inevitable impurities brought into the steel are included in the steel depending on the production raw materials, materials, production equipment, etc. Is done.

  The steel material for cold working according to the present invention may further include Al: 0.2% or less (not including 0%), Zr: 0.2% or less (0%), if necessary, with respect to the basic component. ), Ti: 0.2% or less (not including 0%), Nb: 0.5% or less (not including 0%), V: 0.5% or less (including 0%) No), Ta: 0.1% or less (excluding 0%), Hf: 0.1% or less (not including 0%), or B: 0.002% or less (not including 0%). ) Can be additionally added depending on the purpose, as described below. These elements may be used alone or in combination of two or more.

  However, when these elements are added together, it is necessary and effective to satisfy the following formula (2) in relation to the N amount.

  Al, Zr, Ti, Nb, V, Ta, Hf and B have a strong affinity with N, and coexist with N to form an N compound and reduce the amount of dissolved N. Regulated as above. However, it is effective to pay attention to the following formulation even in a range below this upper limit.

Al: preferably 0.05% or less, more preferably 0.03% or less Zr: preferably 0.05% or less, more preferably 0.03% or less Ti: preferably 0.05% or less, more preferably 0 0.03%
Nb: preferably 0.3% or less, more preferably 0.1% or less V: preferably 0.3% or less, more preferably 0.1% or less Ta: preferably 0.04% or less, more preferably 0 0.02% or less Hf: preferably 0.04% or less, more preferably 0.02% or less B: preferably 0.001% or less, more preferably 0.0008% or less
On the other hand, the production of N compounds of these elements effectively functions to refine steel grains and improve the toughness of parts obtained after cold working, and at the same time improve crack resistance. Therefore, although the upper limit of content of each element is as described above, a more preferable following range may be selected as needed as long as the upper limit is not exceeded.

Al: preferably 0.002% or more, more preferably 0.004% or more Zr: preferably 0.002% or more, more preferably 0.004% or more Ti: preferably 0.002% or more, more preferably 0 0.004% or more Nb: preferably 0.001% or more, more preferably 0.002% or more V: preferably 0.001% or more, more preferably 0.002% or more Ta: preferably 0.001% or more, More preferably 0.002% or more Hf: preferably 0.001% or more, more preferably 0.002% or more B: preferably 0.0001% or more, more preferably 0.0002% or more In the present invention, As for the basic steel composition, the following formula (2) is obtained based on the same grounds when adding the above-mentioned selective elements, as the condition of formula (1) is added with respect to the ratio of Sn and solute N as an essential component. Subject to being satisfied.

N (%)-{14 * Al (%) / 27 + 14 * Ti (%) / 47.9
+ 14 * Nb (%) / 92.9 + 14 * V (%) / 50.9
+ 14 * Zr (%) / 91.2 + 14 * B (%) / 100.8
+ 14 * Ta (%) / 180.9 + 14 * Hf (%) / 178.5}
≧ 0.006% (2)
The coefficient in the above equation is a value obtained by dividing the atomic weight of an element having a strong affinity with N, for example, Al by the atomic weight of N. The symbol * means a product (x).

  This condition will be described. The steel of the present invention is characterized by containing a solid solution N amount of 0.006% or more as described above. In order to secure this solid solution N amount, It is required to increase the amount and reduce the elements having high affinity with N. Therefore, when a selective element having a strong affinity with N as described above is added to Sn, it is necessary to secure a solid solution N amount of 0.006% or more for each content.

  That is, it is to increase the total amount of N in the steel and to reduce elements having a high affinity for N. When the steel contains an element having a strong affinity for N such as Al, N is an N compound such as Al. And the amount of solute N is reduced. Therefore, if the total amount of N in the steel is made larger than that, even if all Al and the like form N and N compounds, a sufficient amount of dissolved N can be secured.

  The above equation (2) indicates this condition. If the addition amount of the selected element is calculated and blended based on this formula, the required total N amount in the manufactured steel material, and therefore, the solid solution N amount of 0.006% or more can be secured.

Next, in addition to the above components, the steel material for cold working according to the present invention, if necessary, Cr: 2% or less (not including 0%), Cu: 5% or less (not including 0%) Ni: 5% or less (not including 0%) and / or Co: 5% or less (not including 0%), Mo: 2% or less (not including 0%) and / or W: 2 % Or less (not including 0%) is effective. Each will be described below.
・ Cr: 2% or less (excluding 0%)
Cr is an element that improves the deformability of the steel by increasing the strength of the crystal grain boundary, and may be contained by 0.1% or more, more preferably 0.2% or more, if necessary. However, excessive addition of Cr increases deformation resistance and decreases cold workability, so it is preferably 1.5% or less, more preferably 1% or less.
Cu: 5% or less (excluding 0%)
Cu can improve the strength of parts after processing by the effect of hardening steel by strain aging. Preferably 0.1% or more, more preferably 0.5% or more. However, even if it is added excessively, the effect is saturated, and an effect commensurate with the content cannot be expected.Instead, the cold workability is deteriorated and the surface properties of the parts are deteriorated. 5%, preferably 4% or less, more preferably 3% or less.
Ni: 5% or less and / or Co: 5% or less (excluding 0%)
Ni is effective in improving the deformability of ferrite-pearlite steel, and is effective in preventing surface defects generated on the steel material surface when co-added with Cu, preferably 0.1% or more, more preferably Is preferable to contain 0.5% or more. In addition, when adding Cu, it is good to add Ni of the same quantity as Cu, or about 70% of it. However, even if added over 5%, the effect is saturated and conversely the cold workability deteriorates, so the upper limit is made 5%, preferably 4% or less, more preferably 3% or less.

Co, like Ni, is effective in improving the deformability of the ferrite-pearlite steel, and is preferably 0.1% or more, more preferably 0.5% or more. However, if it exceeds 5%, the grain boundary strength is lowered in the manufacturing process such as casting and rolling, and cracking is likely to occur, so 5% is the upper limit, preferably 4% or less, more preferably 3% or less. .
Mo: 2% or less and / or W: 2% or less (excluding 0%)
Mo has the effect | action which increases the hardness and deformability of the steel materials after a process, Preferably it is 0.04% or more, More preferably, it can contain 0.08% or more. However, since addition exceeding 2% deteriorates cold workability, the upper limit is 2%, preferably 1.5% or less, more preferably 1% or less.

  W, like Mo, has the effect of increasing the hardness and deformability after processing, preferably 0.04% or more, more preferably 0.08% or more, but more than 2% addition In order to deteriorate cold workability, the upper limit is 2%, preferably 1.5% or less, more preferably 1% or less.

In addition to the above components, the steel for cold working according to the present invention may further include, if necessary, Ca: 0.05% or less (not including 0%), REM: 0.05% or less (not including 0%) ), Mg: 0.02% or less (not including 0%), Li: 0.02% or less (not including 0%), Pb: 0.3% or less (not including 0%) It is also effective to contain one or more selected from the group consisting of Bi: 0.2% or less (excluding 0%) depending on the purpose. Each will be described below.
Ca: 0.05% or less (excluding 0%)
Ca is an element that spheroidizes sulfide compound inclusions such as MnS and improves the deformability of the steel and contributes to improvement of machinability, and is preferably 0.005% or more, more preferably 0.01%. The above can be contained. However, even if added excessively, the effect is saturated and an effect commensurate with the amount added cannot be expected. Therefore, the upper limit is set to 0.05%, preferably 0.04% or less, more preferably 0.03% or less. .
REM: 0.05% or less (excluding 0%)
Since REM also spheroidizes sulfide compound inclusions such as MnS and improves the deformability of steel and contributes to the improvement of machinability, it is preferably 0.005% or more, more preferably 0.01%. The above can be contained. However, even if added excessively, the effect is saturated and an effect commensurate with the amount added cannot be expected, so the upper limit is 0.05%, preferably 0.04% or less, more preferably 0.03% or less. .
Mg: 0.02% or less (excluding 0%)
Mg, like Ca, spheroidizes sulfide compound inclusions such as MnS and improves the deformability of the steel and contributes to the improvement of machinability. Therefore, it is preferably 0.002% or more, more preferably 0.005%. The above can be contained. However, even if added excessively, the effect is saturated and an effect commensurate with the amount added cannot be expected, so the upper limit is 0.02%, preferably 0.018% or less, more preferably 0.015% or less. .
Li: 0.02% or less (excluding 0%)
Li can spheroidize sulfide compound inclusions, such as MnS, like Ca, and can improve the deformability of steel. Also, it lowers the melting point of Al oxide and renders it harmless, improving machinability. Therefore, it is preferable to contain 0.002% or more, more preferably 0.005% or more. However, even if added excessively, the effect is saturated and an effect commensurate with the amount added cannot be expected, so the upper limit is 0.02%, preferably 0.018% or less, more preferably 0.015% or less. .
Pb: 0.3% or less (excluding 0%)
Pb can be added as a machinability improving element, preferably 0.01% or more, more preferably 0.02% or more. However, if it exceeds 0.3%, problems in production such as rolling mills occur, so the upper limit is made 0.3%, preferably 0.28% or less, more preferably 0.25% or less.
-Bi: 0.2% or less (excluding 0%)
Bi is also effective for improving the machinability like Pb, and is preferably 0.01% or more, more preferably 0.02% or more. However, if it exceeds 0.2%, the effect is increased. For saturation, the upper limit is set to 0.2%, preferably 0.18% or less, more preferably 0.15% or less.

  In addition, since these arbitrary elements below Ca are alloying agents mixed according to the purpose, there are few restrictions on the relationship with the amount of N as in the case of selectively mixing Al, Ti, etc. , Regulation like the previous formula (2) is not necessary.

  Next, the present invention includes a product part that is obtained by cold-working the steel having the characteristics described above in detail at a temperature limited to 200 ° C. or less. Since this cold working temperature naturally affects the cold workability, the upper limit value is limited to 200 ° C., preferably 180 ° C., more preferably 160 ° C. In cold working at higher temperatures, dynamic strain aging occurs during deformation, the deformation resistance increases, and the mold life deteriorates.

  The component product of the present invention obtained under such conditions is characterized in that it has a strength satisfying the following formula (3) in relation to the deformation resistance during cold working. The strength (Hv) means a level that can be satisfactorily satisfied for this kind of steel part for cold working.

H ≧ (DR + 1000) / 6 (3)
H: Strength of parts after cold working (Hv)
DR: Deformation resistance during cold working (MPa)
The cold working method here includes cold forging, cold forging, cold rolling, cold drawing or cold extrusion. Further, if necessary for the processing of the parts, processing such as wire drawing and rolling may be performed. Although cold working is usually performed at room temperature, the deformation resistance increases conversely due to the influence of temperature dependence below 0 ° C., so the preferred lower limit of the working temperature is 0 ° C. The processing temperature is the atmospheric temperature of the steel material during processing.
As described above, the present invention has excellent cold workability characterized by containing Sn and at the same time regulating the quantitative relationship between the Sn content and the total contained N and solute N. It is a steel material. In addition, as described above, product parts manufactured from this steel material have good strength, but depending on the intended part, if the above strength or more appropriate deformation resistance is required by the material steel, or depending on other circumstances In addition, the following measures can be additionally implemented.

  That is, the steel for cold working of the present invention described above is heated to a temperature of the Ac1 point or higher and then subjected to the required hot working in this temperature range as it is or after cooling at 1 ° C./S or lower. It is good to cool to 500 ° C. or less at a speed.

  This method is based on various heat treatments such as normalizing treatment, light annealing (LA) treatment, spheroidizing treatment, etc., and at a heating temperature of Ac1 point + 25 ° C. to 50 ° C. to 500 ° C., 10 to 30 Heat treatment for at least 4 minutes and at most 4 minutes is sufficient. In addition, hot working such as wire drawing, rolling, or pressing can be appropriately performed during the heating and holding.

  The following examples also illustrate heat treatment or thermomechanical treatment of such steel materials, but the present invention does not require such additional heat treatments, and the steel materials themselves as already detailed. It goes without saying that the cold workability that is excellent in strength, deformation resistance and the like is exhibited due to the above characteristics.

  100 types of test steels of steel symbols 1A to 4T having the composition described in Tables 1 to 4 were billeted by vacuum furnace melting and hot forging, and billet welded. Rolled.

  In the “component range” column in Tables 1 to 4, an example in which the content of any of the component elements deviates from the regulation range of the present invention is noted, and the “x” mark is attached. It points out that it is steel as a comparative example. “O” and “X” in the “determination based on the formulas (1) and (2)” satisfy the above two formulas (1) and (2) in which the quantitative conditions of the component elements regulate the regulation scope of the present invention. Instruct whether or not. Further, “N” in the table indicates the total N amount. In addition, the “solid solution N amount” described in the table is a value measured by a method based on JIS G 1228 described above.

  Next, of each of the above 100 types of rolled wire rods, some of the wire rods marked with (j) in the “Manufacturing method” column in the same table are left unrolled without any heat treatment. As shown in Table 5 (a) to (i), the wires were subjected to heat treatment at different heating temperatures of 800 to 1100 ° C. for comparison purposes. Half of them (b, d, g) were simply heat treatment, and the others were heat treated at the heating temperature. In addition, after the said heat processing cooled to 430-500 degreeC, the retention time for 30 minutes was provided.

  Next, a test piece of φ6 mm × 9 mmL is cut out from the center portion of each heat-treated wire and as-rolled wire, and each test piece is compressed by cold forging using a 200 KN processing formaster test device. processed. The conditions for cold forging were a processing strain rate of about 10 / S, a processing temperature of 20 to 200 ° C., and a compression ratio of 20 to 80%. The processing strain rate is an average value of strain rates during processing (plastic deformation).

  About each obtained part, the presence or absence of the crack was confirmed by observing the surface by the observation magnification of 20 times with the stereomicroscope. Tables 6 and 7 show the processing conditions, presence / absence of cracks, and deformation resistance of each part.

  In addition, using a Vickers hardness tester, the Vickers hardness of each part under the conditions of load: 1000 g, measurement position: D / 4 position center of test piece cross section (D: part diameter) and number of measurements: 5 times (Hv) was measured and similarly displayed in Tables 6 and 7.

  Evaluation of these series of test results was performed by using a steel (particularly, one that satisfies the condition given by the previous formula (3)) that has no cracks in the part and that has a low deformation resistance against the part hardness. It was determined that the material was excellent in workability, and “◯” was displayed. On the other hand, in the test piece of the comparative example which does not satisfy the condition of the formula (3), “×” is displayed for the cracked one. For reference, the formula is rewritten here.

H ≧ (DR + 1000) / 6 (3)
H: Strength of parts after cold working (Hv)
DR: Deformation resistance during cold working (MPa)
As is apparent from Tables 6 and 7, in the preferred processing conditions (compression rate and processing temperature), all of the example steels satisfying the requirements of the chemical component amount and the solute N amount specified by the present invention are cold workability. It can be seen that all of the component products obtained from this have secured high strength. In addition, when trying to secure a component strength comparable to this high strength, it is necessary to use a steel material having a higher deformation resistance, which inevitably leads to a reduction in the life of the mold. In this respect, the excellent cold workability of the steel of the present invention is well understood. This point will be discussed below for each comparative material.

  In addition, among the said Example, the steel materials equivalent to ai which heat-processed with respect to as-rolled steel materials have shown the performance in which the quality is as good as the former, and the steel materials of this invention However, it can be seen that a part can be formed as it is without rolling.

  No. 3 is an example using steel symbol 1C with a small amount of Mn. Since Mn exceeds a predetermined range, cracks are generated.

  No. 7 is an example using the steel symbol 1G with a large amount of C. Since C exceeds a predetermined range, cracks occur.

  No. 9 is an example using the steel symbol 1I with a large amount of Sn. Since Sn exceeds a predetermined range, a crack is generated.

  No. 21 is an example using steel symbol 1U with a large amount of Si, and cracks have occurred because Si exceeds a predetermined range.

  No. 42 is an example using the steel symbol 2P with a small amount of Si. Since Si is less than a predetermined range, cracks are generated.

  No. 51 is an example using the steel symbol 2Y with a large amount of Mn. Since Mn exceeds a predetermined range, cracks are generated.

  No. No. 67 is an example using a steel symbol 3O with a large amount of N, and cracks occur because N exceeds a predetermined range.

  No. 71 is an example using the steel symbol 3S with a large amount of Sn, and cracks occur because Sn exceeds a predetermined range.

  No. 86 is an example using the steel symbol 4H with a large amount of S, and cracks occur because S exceeds a predetermined range.

  No. 96 is an example using the steel symbol 4R with a large amount of P, and cracks occur because P exceeds a predetermined range.

  No. No. 98 is an example using steel symbol 4V with a small amount of C. Since C is less than a predetermined range, cracks are generated.

  No. 44, no. 61, no. 62, no. 74, no. 75, no. 77 and No. 80 is an example in which steels 2R, 3I, 3J, 3V, 3W, 3Y and 4B having a small amount of dissolved N are used. In any case, the amount of solute N is less than the predetermined range and does not satisfy the condition of the expression (2), so that it is understood that the condition deviates from the condition of the expression (3) even after processing.

  No. 47, no. 84, no. 85, no. 88 and no. No. 89 has a chemical composition that does not satisfy the condition of the formula (2), so that it can be seen that the deformation resistance is increased and the condition of the formula (3) is deviated even after processing.

Claims (10)

C: 0.06 to 0.5% (mass%, the same shall apply hereinafter), Si: 0.01 to 0.1%, Mn: 0.2 to 1.5%, P: 0.05% or less (0 %), S: 0.05% or less (excluding 0%), Sn: 0.6% or less (excluding 0%), N: 0.04% or less (excluding 0%) Not contained.), The balance is composed of Fe and inevitable impurities, the content of solid solution N (Sol. N) is 0.006% or more, and the ratio of the Sn amount to the solid solution N amount is represented by the following formula ( A steel material excellent in cold workability characterized by satisfying 1).
10 ≦ Sn / Sol. N ≦ 40 (1)   N: The steel material excellent in cold workability of Claim 1 containing 0.007% or more. Al: 0.2% or less (not including 0%), Zr: 0.2% or less (not including 0%), Ti: 0.2% or less (not including 0%), Nb: 0.5% or less (not including 0%), V: 0.5% or less (not including 0%), Ta: 0.1% or less (not including 0%), Hf: 0.00 1 or less (not including 0%) and B: 0.002% or less (not including 0%), containing one or more selective elements selected from the group consisting of N and these selections The steel material having excellent cold workability according to claim 1 or 2, wherein a quantitative relationship with an element satisfies the following formula (2).
N (%)-{14 * Al (%) / 27 + 14 * Ti (%) / 47.9
+ 14 * Nb (%) / 92.9 + 14 * V (%) / 50.9
+ 14 * Zr (%) / 91.2 + 14 * B (%) / 100.8
+ 14 * Ta (%) / 180.9 + 14 * Hf (%) / 178.5}
≧ 0.006% (2)
However, * in a formula represents a product.   The steel material excellent in cold workability according to any one of claims 1 to 3, containing Cr: 2% or less (excluding 0%).   The steel material excellent in cold workability according to any one of claims 1 to 4, containing Cu: 5% or less (excluding 0%).   6. Excellent cold workability according to any one of claims 1 to 5, containing Ni: 5% or less (excluding 0%) and / or Co: 5% or less (excluding 0%). Steel material.   The excellent cold workability according to any one of claims 1 to 6, which contains Mo: 2% or less (excluding 0%) and / or W: 2% or less (excluding 0%). Steel material.   Ca: 0.05% or less (not including 0%), REM: 0.05% or less (not including 0%), Mg: 0.02% or less (not including 0%), Li: Selected from the group consisting of 0.02% or less (excluding 0%), Pb: 0.3% or less (not including 0%), Bi: 0.2% or less (not including 0%) The steel material excellent in cold workability in any one of Claim 1 thru | or 7 containing 1 type, or 2 or more types.   A cold-worked part obtained by cold-working the steel material according to any one of claims 1 to 8 at a working temperature of 200 ° C or lower. The cold-worked component according to claim 9, wherein the strength satisfies the relationship of the following expression (3) with respect to the deformation resistance during cold work.
H ≧ (DR + 1000) / 6 (3)
H: Strength of parts after cold working (Hv)
DR: Deformation resistance during cold working (MPa)