Patent Application
20160319393
The present invention relates to a rolled material for high strength spring, and a wire for high strength spring using the same. More particularly, the present invention relates to a rolled material and a wire, which are useful as raw materials of high strength springs that are used in a state of being subjected to heat treatment, namely, quenching and tempering, particularly a rolled material having excellent wire drawability, and a wire for high strength spring, which are excellent in corrosion fatigue properties even though a tensile strength is a high strength in a range of 1,900 MPa or more after wire drawing.
Coil springs used in automobiles, for example, a valve spring and a suspension spring used in the engine, suspension, and the like are required to reduce the weight and to increase the strength so as to achieve exhaust gas reduction and improvement in fuel efficiency. In the manufacture of a high strength wire, wire drawing is applied for the purpose of achieving improvement in dimensional accuracy of a wire diameter and uniformization of a structure due to plastic working before a heat treatment of quenching and tempering. Particularly, a wire drawing reduction rate is sometimes increased so as to further uniformize the structure in the high strength wire, and a rolled material is required to have satisfactory wire drawability. The spring imparted with high strength is likely to cause hydrogen brittleness because of its poor toughness and ductility, leading to degradation of corrosion fatigue properties. Therefore, the steel wire (wire) for high strength spring used in the manufacture of a spring is required to have excellent corrosion fatigue properties. Hydrogen generated by corrosion enters into a steel and may lead to embrittlement of a steel material, thus causing corrosion fatigue fracture, so that there is a need to improve corrosion resistance and hydrogen embrittlement resistance of the steel material so as to improve corrosion fatigue properties.
There has been known, as a method for enhancing wire drawability of a rolled material for high strength spring and corrosion fatigue properties of a wire for high strength spring, a method for controlling by the chemical composition. However, such a method is not necessarily desirable from a viewpoint of an increase in manufacturing costs and resource saving because of use of a large amount of an alloying element.
Meanwhile, there have been known, as a method for manufacturing a spring, a method in which a steel wire is heating to a quenching temperature and hot-formed into a spring shape, followed by oil cooling and further tempering, and a method in which a steel wire is subjected to quenching and tempering, and then cold-formed into a spring shape. In the cold forming method of the latter, it is also known that quenching and tempering before forming is performed by high frequency induction heating. For example, Patent Document 1 discloses technology in which a wire rod is cold-drawn and then the structure is adjusted by quenching and tempering through high frequency induction heating. According to this technology, a structural fraction of pearlite is set at 30% or less and a structural fraction composed of martensite and bainite is set at 70% or more and then cold drawing is performed at a predetermined area reduction rate, followed by quenching and tempering to thereby reduce the unsolved carbides, leading to an improvement in delayed fracture properties.
In Examples of Patent Document 2, a rolled wire rod is subjected to wire drawing, followed by a quenching and tempering treatment through high frequency induction heating. This technology focuses primarily on achievement of the reconciliation of high strength and formability (coiling properties), and gives no consideration to hydrogen embrittlement resistance.
While paying attention to the amount of hydrogen in a steel that is evaluated by the total amount of hydrogen released when the temperature is raised from room temperature to 350° C., Patent Document 3 proposes a hot rolled wire rod having excellent wire drawability under severe wire drawing conditions. However, Patent Document 3 focuses only on wire drawability during special processing such as severe wire drawing, and also gives no consideration to hydrogen embrittlement resistance after quenching and tempering, which becomes most important in a suspension spring.
In light of aforementioned circumstances, the present invention has been made, and it is an object thereof is to provide a rolled material for high strength spring, which is a material for high strength spring including both materials for hot coiling and cold coiling, and which has excellent wire drawability even when suppressing the addition amount of an alloying element, and also can exhibit corrosion fatigue properties after quenching and tempering.
The present invention that can solve the foregoing problems provides a rolled material for high strength spring, including, in % by mass:
P: exceeding 0% and 0.015% or less,
S: exceeding 0% and 0.015% or less,
Ni: 0.1 to 0.80%, with the balance being iron and inevitable impurities, wherein
an amount of nondiffusible hydrogen is 0.40 ppm by mass or less, and
an area ratio of ferrite expressed as a percentage satisfies an inequality expression (1) below, and a total area ratio of bainite and martensite is 2% or less:
Ferrite area ratio<{(0.77−[C])/0.77−[C]/3+0.08}×100 (1)
where [name of element] in the above inequality expression (1) means a content expressed in % by mass of each element.
The rolled material for high strength spring of the present invention preferably includes, in % by mass, at least one belonging to any one of the following (a), (b), (c) and (d):
(a) Cr: exceeding 0% and 1.2% or less,
(b) Ti: exceeding 0% and 0.13% or less,
(c) B: exceeding 0% and 0.01% or less, and
(d) at least one selected from the group consisting of Nb: exceeding 0% and 0.1% or less, Mo: exceeding 0% and 0.5% or less, and V: exceeding 0% and 0.4% or less.
In the rolled material for high strength spring of the present invention, an ideal critical diameter Di is preferably in a range of 65 to 140 mm, and is calculated using an equation (2) below when B is not included or using an equation (3) below when B is included. If some elements are not included in the rolled material of the present invention among elements mentioned in the equations, calculation is made under the condition that the content of the elements is 0%.
D
i=25.4×(0.171+0.001×[C]+0.265×[C]2)×(3.3333×[Mn]1)×(1+0.7×[Si])×(1+0.363×[Ni])×(1+2.16×[Cr])×(1+0.365×[Cu])×(1+1.73×[V])×(1+3×[Mo]) (2)
D
i=25.4×(0.171+0.001×[C]+0.265×[C]2)×(3.3333×[Mn]1)×(1+0.7×[Si])×(1+0.363×[Ni])×(1+2.16×[Cr])×(1+0.365×[Cu])×(1+1.73×[V])×(1+3×[Mo])×(6.849017−46.78647×[C]+196.6635×[C]2−471.3978×[C]3+587.8504×[C]4−295.0410×[C]5) (3)
where [name of element] in the above equations (2) and (3) means a content expressed in % by mass of each element.
The present invention also includes a wire for high strength spring, having a tensile strength of 1,900 MPa or more, obtained by wire-drawing anyone of the rolled materials for high strength spring mentioned above, followed by a quenching and tempering treatment.
According to the present invention, since the amount of nondiffusible hydrogen in a rolled material is suppressed and formation of supercooled structures such as bainite and martensite is suppressed, the rolled material exhibits excellent wire drawability without adding a large amount of an alloying element. In the rolled material of the present invention, an area ratio of ferrite is appropriately adjusted according to the concentration of C, specifically, the area ratio of ferrite decreases as the concentration of C increases, so that a wire obtained by wire-drawing this rolled material, followed by quenching and tempering is excellent in corrosion fatigue properties even though the strength is a high strength in a range of 1,900 MPa or more. In such a rolled material, it is possible to improve wire drawability of the rolled material and corrosion fatigue properties of the wire even when suppressing the cost of steel materials, thus making it possible to supply a high strength spring which is excellent in manufacturability and is very unlikely to cause corrosion fatigue fracture, for example, a coil spring such as a suspension spring that is one of automobile components, at a cheap price.
Wire drawability of a rolled material is usually influenced by ductility of the rolled material. Poor ductility of a basis material or degradation of ductility due to the presence of a supercooled structure may lead to fracture during wire drawing, resulting in drastic degradation of manufacturability. Therefore, wire drawability can be improved by enhancing ductility of the rolled material.
Meanwhile, if corrosion occurs, pits are generated on a surface of a steel material, and wall thinning due to corrosion may lead to a decrease in wire diameter of the steel material. Hydrogen generated by corrosion enters into a steel and may lead to embrittlement of the steel material. Corrosion fatigue fracture occurs with these corrosion pits, wall thickness reduction sections, and embrittled sections of the steel material as starting points. Therefore, corrosion fatigue fracture can be improved by improving hydrogen embrittlement resistance and corrosion resistance of the steel material.
The inventors of the present invention have made a study of factors that exert an influence on ductility, hydrogen embrittlement resistance and corrosion resistance of a steel material from various viewpoints. As a result, they have found that proper control of both a ferrite area ratio of a rolled material and the amount of hydrogen in a steel expressed particularly by the amount of nondiffusible hydrogen enables an improvement in ductility of the rolled material and significant improvement in hydrogen embrittlement resistance when the rolled material is subjected to wire drawing, followed by quenching and tempering. They have also found that corrosion resistance can also be improved by appropriately adjusting the chemical composition, leading to significant improvement in corrosion fatigue properties, thus completing the present invention. The structure, the amount of hydrogen in steel, and the chemical composition of the rolled material of the present invention will be sequentially described below.
The ferrite structure is likely to form a carbide depleted region after quenching and tempering, and formation of the carbide depleted region serves as a fracture starting point, as a strength lowering section. While carbides are capable of detoxicating hydrogen by trapping hydrogen, the carbide depleted region becomes an area lacking such a capability, so that hydrogen embrittlement is likely to occur, leading to fracture. In order to suppress formation of the carbide depleted region after a quenching and tempering treatment to thereby uniformly disperse carbides, there is a need to form a structure in which carbides are uniformly dispersed in a stage of a rolled material before quenching and tempering. Namely, there is a need that a ratio of a pearlite structure, which is a structure that ferrite and carbides form layers, is increased to thereby decrease a ratio of a ferrite structure. The inventors of the present invention have found that it is important to make an area ratio of the ferrite structure smaller than that of the ferrite structure obtained by allowing to cool after rolling, so as to improve hydrogen embrittlement resistance, and that the ferrite structure obtained by allowing to cool after rolling has a close relation with the amount of C.
As a result of examination of the ratio of the ferrite structure obtained by allowing to cool after rolling with respect to a steel material in which the amount of C is variously changed, it became clear that the ratio of the ferrite structure obtained by allowing to cool after rolling is represented by the right side of an inequality expression (1) below. The rolled material of the present invention is characterized by controlling the ratio of the ferrite structure so as to satisfy the inequality expression (1) below. The [name of element] in the inequality expression (1) below means a content expressed in % by mass of each element. As used herein, the ferrite area ratio means a ratio expressed as a percentage.
Ferrite area ratio<{(0.77−[C])/0.77−[C]/3+0.08}×100 (1)
Regarding the rolled material of the present invention, the ratio of the ferrite structure is preferably reduced by at least 10% lower than that of the ferrite structure obtained by allowing to cool after rolling, namely, the ratio of the ferrite structure preferably satisfies an inequality expression (1-2) below.
Ferrite area ratio{(0.77−[C])/0.77−[C]/3+0.08}×100×0.9 (1−2)
In the rolled material of the present invention, when the content of supercooled structures such as bainite and martensite increases, wire drawability is drastically degraded. Therefore, even if supercooled structures are included, the area percentage is 2 percentage or less, preferably 1 percentage or less, most preferably 0 percentage or less.
In the rolled material of the present invention, formation of ferrite, bainite and martensite is suppressed, and the structure except for them is pearlite.
The amount of hydrogen in the rolled material of the present invention will be described below. In the rolled material of the present invention, an amount of nondiffusible hydrogen is set at 0.40 ppm by mass or less. If a large amount of nondiffusible hydrogen exists, hydrogen is accumulated around inclusions and segregating zones in the rolled material to thereby generate microcracks, resulting in degraded wire drawability of the rolled material. If a large amount of nondiffusible hydrogen exists, a permissible amount of hydrogen, which further enters until the steel material embrittles, decreases. Therefore, even though a small amount of hydrogen entered during use as a spring, embrittlement of the steel material occurs and early fracture is likely to occur, resulting in degraded hydrogen embrittlement resistance. The amount of nondiffusible hydrogen is preferably 0.35 ppm by mass or less, and more preferably 0.30 ppm by mass or less. The less the amount of nondiffusible hydrogen, the better. However, it is difficult to set at 0 ppm by mass and the lower limit is about 0.01 ppm by mass.
The amount of nondiffusible hydrogen is an amount of hydrogen measured by the method mentioned in Examples below, and specifically means the total amount of hydrogen released at 300 to 600° C. when the temperature of a steel material is raised at 100° C./hour.
The rolled material for high strength spring according to the present invention is a low alloy steel in which the content of an alloying element is suppressed, and the chemical composition is as follows. The present invention also includes a wire obtained by wire-drawing the above-mentioned rolled material, followed by quenching and tempering, and the chemical composition is the same as that of the rolled material.
Carbon is an element that is required to ensure the strength of a wire for spring, and is also required to generate fine carbides that serve as hydrogen trapping sites. From such a viewpoint, the amount of C is determined in a range of 0.39% or more. The lower limit of the amount of C is preferably 0.45% or more, and more preferably 0.50% or more. Excessive C amount, however, might generate coarse residual austenite and unsolved carbides after quenching and tempering, which further degrades hydrogen embrittlement resistance. C is an element that degrades corrosion resistance, so that there is a need to suppress the amount of C so as to enhance corrosion fatigue properties of a spring product such as a suspension spring which is a final product. From such a viewpoint, the amount of C is determined in a range of 0.65% or less. The upper limit of the amount of C is preferably 0.62% or less, and more preferably 0.60% or less.
Si is an element that is required to ensure the strength, and also exhibits the effect of refining carbides. To effectively exhibit these effects, the amount of Si is determined in a range of 1.5% or more. The lower limit of the amount of Si is preferably 1.7% or more, and more preferably 1.9% or more. Meanwhile, since Si is also an element that accelerates decarburization, excessive Si amount accelerates formation of a decarburized layer on a surface of a steel material, thus requiring the peeling step for removal of the decarburized layer, resulting in increased manufacturing costs. Unsolved carbides also increase, thus degrading hydrogen embrittlement resistance. From such a viewpoint, the amount of Si is determined in a range of 2.5% or less. The upper limit of the amount of Si is preferably 2.3% or less, more preferably 2.2% or less, and still more preferably 2.1% or less.
Mn is an element that is employed as a deoxidizing element and reacts with S, which is a harmful element in a steel, to form MnS, and is useful for detoxication of S. Mn is also an element that contributes to an improvement in strength. To effectively exhibit these effects, the amount of Mn is determined in a range of 0.15% or more. The lower limit of the amount of Mn is preferably 0.2% or more, and more preferably 0.3% or more. Excessive Mn amount, however, degrades toughness, thus causing embrittlement of a steel material. From such a viewpoint, the amount of Mn is determined in a range of 1.2% or less. The upper limit of the amount of Mn is preferably 1.0% or less, more preferably 0.85% or less, and still more preferably 0.70% or less.
P: exceeding 0% and 0.015% or less
P is a harmful element that degrades ductility such as coiling properties of a rolled material, namely, a wire rod, and the amount thereof is preferably as small as possible. P is likely to segregate in grain boundaries to cause grain boundary embrittlement, and hydrogen is likely to cause fracture of grain boundaries, thus exerting an adverse influence on hydrogen embrittlement resistance. From such a viewpoint, the amount of P is determined in a range of 0.015% or less. The upper limit of the amount of P is preferably 0.010% or less, and more preferably 0.008% or less. The amount of P is preferably as small as possible, and is usually about 0.001%.
S: exceeding 0% and 0.015% or less
Like P mentioned above, S is a harmful element that degrades ductility such as coiling properties of a rolled material, and the amount thereof is preferably as small as possible. S is likely to segregate in grain boundaries to cause grain boundary embrittlement, and hydrogen is likely to cause fracture of grain boundaries, thus exerting an adverse influence on hydrogen embrittlement resistance. From such a viewpoint, the amount of S is determined in a range of 0.015% or less. The upper limit of the amount of S is preferably 0.010% or less, and more preferably 0.008% or less. The amount of S is preferably as small as possible, and is usually about 0.001%.
Al is mainly added as a deoxidizing element. This element reacts with N to form AlN to thereby detoxicate solid-saluted N, and also contributes to refining of the structure. To adequately exhibit these effects, the amount of Al is determined in a range of 0.001% or more. The lower limit of the amount of Al is preferably 0.002% or more, and more preferably 0.005% or more. However, since Al is an element that accelerates decarburization, like Si, there is a need to suppress the amount of Al in a steel for spring, which includes a large amount of Si. Therefore, in the present invention, the amount of Al is determined in a range of 0.1% or less. The upper limit of the amount of Al is preferably 0.07% or less, more preferably 0.030% or less, and particularly preferably 0.020% or less.
Cu is an element that is effective in suppressing surface decarburization and improving corrosion resistance. Therefore, the amount of Cu is determined in a range of 0.1% or more. The lower limit of the amount of Cu is preferably 0.15% or more, more preferably 0.20% or more, and still more preferably 0.25% or more. Excessive Cu amount, however, causes cracks during hot working and increases costs. Therefore, the amount of Cu is determined in a range of 0.80% or less. The upper limit of the amount of Cu is preferably 0.70% or less, more preferably 0.60% or less, still more preferably 0.48% or less, particularly preferably 0.35% or less, and most preferably 0.30% or less.
Like Cu, Ni is an element that is effective in suppressing surface decarburization and improving corrosion resistance. Therefore, the amount of Ni is determined in a range of 0.1% or more. The lower limit of the amount of Ni is preferably 0.15% or more, more preferably 0.20% or more, and still more preferably 0.35% or more, and most preferably 0.45% or more. Excessive Ni amount, however, increases costs. Therefore, the amount of Ni is determined in a range of 0.80% or less. The upper limit of the amount of Ni is preferably 0.70% or less, more preferably 0.60% or less, still more preferably 0.55% or less, and yet preferably 0.48% or less, 0.35% or less, and 0.30% or less.
Basic components of the rolled material of the present invention are as mentioned above, the balance being substantially iron. As a matter of course, including of inevitable impurities introduced by the state of raw material, material, manufacturing facility, and the like is permitted. The rolled material for spring of the present invention has the chemical composition mentioned above even when suppressing an alloying element such as Cu, and can achieve excellent coiling properties and hydrogen embrittlement resistance while having high strength. Elements mentioned below may be further included for the purpose of improving corrosion resistance according to application.
Cr: exceeding 0% and 1.2% or less
Cr is an element that is effective in improving corrosion resistance. To effectively exhibit these effects, the amount of Cr is preferably 0.01% or more, more preferably 0.05% or more, and still more preferably 0.10% or more. However, Cr is an element that has a strong tendency to form carbides, and forms peculiar carbides in a steel material and is likely to be dissolved in cementite in a high concentration. It is effective to include a small amount of Cr, however, the heating time of the quenching step decreases in high frequency induction heating, leading to insufficient austenitizing of dissolving carbide, cementite, and the like into a base material. Therefore, when including a large amount of Cr, dissolving residue of cementite, in which Cr-based carbide and metallic Cr in high concentration are solid-soluted, is generated as a stress concentration source, so that fracture likely to occur, thus degrading hydrogen embrittlement resistance. Therefore, the amount of Cr is preferably 1.2% or less, more preferably 0.8% or less, and still more preferably 0.6% or less.
Ti: exceeding 0% and 0.13% or less
Ti is an element that is useful to react with S to form sulfide to thereby detoxicate S. Ti also has the effect of refining the structure by forming carbonitride. To effectively exhibit these effects, the amount of Ti is preferably 0.02% or more, more preferably 0.05% or more, and still more preferably 0.06% or more. Excessive Ti amount, however, may form coarse Ti sulfide, thus degrading ductility. Therefore, the amount of Ti is preferably 0.13% or less. From a viewpoint of cost reduction, the amount of Ti is preferably 0.10% or less, and more preferably 0.09% or less.
B: exceeding 0% and 0.01% or less
B is an element that improve hardenability and strengthens prior austenite crystal grain boundaries, and also contributes to suppression of fracture. To effectively exhibit these effects, the amount of B is preferably 0.0005% or more, and more preferably 0.0010% or more. Excessive B amount, however, causes saturation of the above effects, so that the amount of B is preferably 0.01% or less, more preferably 0.0050% or less, and still more preferably 0.0040% or less.
Nb: exceeding 0% and 0.1% or less
Nb is an element that forms carbonitride together with C and N, and mainly contributes to refining of the structure. To effectively exhibit these effects, the amount of Nb is preferably 0.003% or more, more preferably 0.005% or more, and still more preferably 0.01% or more. Excessive Nb amount, however, form coarse carbonitride, thus degrading ductility of a steel material. Therefore, the amount of Nb is preferably 0.1% or less. From a viewpoint of cost reduction, the amount is preferably set at 0.07% or less.
Mo: exceeding 0% and 0.5% or less
Like Nb, Mo is also an element that forms carbonitride together with C and N, and contributes to refining of the structure. Mo is an element that is also effective in ensuring the strength after tempering. To effectively exhibit these effects, the amount of Mo is preferably 0.15% or more, more preferably 0.20% or more, and still more preferably 0.25% or more. Excessive Mo amount, however, form coarse carbonitride, thus degrading ductility such as coiling properties of a steel material. Therefore, the amount of Mo is preferably 0.5% or less, and more preferably 0.4% or less.
V: exceeding 0% and 0.4% or less
V is an element that contributes to an improvement in strength and refining of crystal grains. To effectively exhibit these effects, the amount of V is preferably 0.1% or more, more preferably 0.15% or more, and still more preferably 0.20% or more. Excessive V amount, however, increases costs. Therefore, the amount of V is preferably 0.4% or less, and more preferably 0.3% or less.
Nb, Mo and V may be included individually, or two or more kinds of them may be included in combination.
The rolled material of the present invention includes 0 and N as inevitable impurities, and the amount of them is preferably adjusted in a range mentioned below.
O: exceeding 0% and 0.002% or less
Excess amount of O forms oxide inclusions such as coarse Al2O3 and exerts an adverse influence on fatigue properties. Therefore, the upper limit of the amount of O is preferably 0.002% or less, more preferably 0.0015% or less, and still more preferably 0.0013% or less. Meanwhile, the lower limit of the amount of O is generally 0.0002% or more (preferably 0.0004% or more) from an industrial viewpoint.
N: exceeding 0% and 0.007% or less
As the amount of N increases, it forms coarse nitride together with Ti and Al, thus exerting an adverse influence on fatigue properties. Therefore, the amount of N is preferably as small as possible, for example, 0.007% or less, and more preferably 0.005% or less. Meanwhile, if the amount of N is too reduced, productivity is drastically degraded. N forms nitride together with Al to thereby contribute to refining of crystal grains. From such a viewpoint, the amount of N is preferably 0.001% or more, more preferably 0.002% or more, and still more preferably 0.003% or more.
In the rolled material and the wire of the present invention, an ideal critical diameter Di represented by the equation (2) or (3) below is preferably in a range from 65 to 140 mm. To use the rolled material as a raw material for spring after wire drawing without being subjected to soft annealing, there is a need to reduce supercooled structures to a predetermined content or less so as not to cause wire breakage during wire drawing. If the ideal critical diameter Di is large, hardenability is enhanced and supercooled structures are likely to be generated, so that the upper limit of the ideal critical diameter Di is preferably 140 mm or less. The upper limit of the ideal critical diameter Di is more preferably 135 mm or less, still more preferably 130 mm or less, and particularly preferably 120 mm or less. To perform quenching to the inside as a spring, it is important to ensure given hardenability. Therefore, the lower limit of the ideal critical diameter Di is preferably 65 mm or more, more preferably 70 mm or more, and still more preferably 80 mm or more.
When including no B, the following equation (2) defined in ASTM A255 is used as the ideal critical diameter Di. When including B, there is a need to add a boron factor B.F. defined in ASTM A255-02 by multiplying right side of the equation (2) by the boron factor, and the ideal critical diameter Di is calculated by the following equation (3).
D
i=25.4×(0.171+0.001×[C]+0.265×[C]2)×(3.3333×[Mn]1)×(1+0.7×[Si])×(1+0.363×[Ni])×(1+2.16×[Cr])×(1+0.365×[Cu])×(1+1.73×[V])×(1+3×[Mo]) (2)
D
i=25.4×(0.171+0.001×[C]+0.265×[C]2)×(3.3333×[Mn]1)×(1+0.7×[Si])×(1+0.363×[Ni])×(1+2.16×[Cr])×(1+0.365×[Cu])×(1+1.73×[V])×(1+3×[Mo])×(6.849017−46.78647×[C]+196.6635×[C]2−471.3978×[C]2+587.8504×[C]4−295.0410×[C]5) (3)
where [name of element] in the above equations (2) and (3) means a content expressed in % by mass of each element.
A method for producing a rolled material of the present invention will be described below. In a series of steps of melting a steel having the above chemical composition, followed by continuous casting, blooming, and hot rolling, it is possible to control the amount of nondiffusible hydrogen of the rolled material by adjusting at least one of (A) the amount of hydrogen in a molten steel stage, (B) the homogenizing treatment temperature and time before blooming, and (C) the average cooling rate in a range of 400 to 100° C. after hot rolling. It is also possible to adjust the structure of the rolled material, namely, ferrite, martensite and bainite in the range mentioned above by adjusting all of (i) the coiling temperature (TL) after rolling, (ii) the average cooling rate in a range of TL to 650° C., and (iii) the average cooling rate in a range of 650 to 400° C.
There is a need to remove hydrogen in a steel by diffusion so as to reduce hydrogen in the steel after solidification, and heating at a high temperature for a long time is effective to increase a diffusion rate of hydrogen so as to release hydrogen from a surface of a steel material. Specific examples of the method of reducing the amount of hydrogen in the steel include a method of adjusting in a molten steel stage, a method of adjusting in a stage of a continuously cast material at 1,000° C. or higher after solidification, a method of adjusting in a heating stage before hot rolling, a method of adjusting in a heating stage during rolling, and a method of adjusting in a cooling stage after rolling. It is particularly preferred to perform at least one of treatments for reducing nondiffusible hydrogen (A) to (C) mentioned below.
(A) A degassing treatment is performed by a molten steel treatment to thereby adjust the amount of hydrogen in a molten steel at 2.5 ppm by mass or less.
For example, it is effective that a vacuum tank equipped with two immersion tubes is mounted in a ladle in a secondary refining step and then an Ar gas is blown from the side of one immersion tube, followed by vacuum degassing that enables circulation of a molten steel to the vacuum tank utilizing the buoyancy. This method is excellent in hydrogen removing capability and reduction in inclusion. The amount of hydrogen in the molten steel is preferably 2.0 ppm by mass or less, more preferably 1.8 ppm by mass or less, still more preferably 1.5 ppm by mass or less, and particularly preferably 1.0 ppm by mass or less.
(B) A homogenizing treatment before blooming is performed at 1,100° C. or higher, and preferably 1,200° C. or higher for 10 hours or more.
(C) An average cooling rate in a range of 400 to 100° C. after rolling is set at 0.5° C./second or less, and preferably 0.3° C./second or less.
When a steel material has a large cross-sectional area, particularly, it becomes necessary to perform heating for a long time. If the steel material is heated for a long time, decarburization is accelerated, so that the amount of hydrogen in the steel is preferably reduced by performing the treatment (A) mentioned above.
To adjust an area ratio of the structure in the rolled material, namely, ferrite, bainite and martensite in the range mentioned above, it is preferred to adjust rolling conditions as follows, and to adjust to rolling conditions that satisfy all conditions (i) to (iii).
(i) Coiling temperature TL before initiation of cooling: 900° C. or higher
To reduce the ratio of ferrite, there is a need that the coiling temperature TL before initiation of cooling is adjusted at a temperature in an austenitic single phase. Therefore, TL is more preferably 910° C. or higher, and still more preferably 930° C. or higher. The upper limit of TL is not particularly limited and is about 1,000° C., although it depends on a finish rolling temperature.
(ii) Average cooling rate in a range of TL to 650° C.: 2 to 5° C./second
To allow pearlite transformation to take place, there is a need to suppress formation of ferrite by increasing a cooling rate in a temperature range of TL to 650° C. Therefore, an average cooling rate in a range of TL to 650° C. is preferably 2° C./second or more, more preferably 2.3° C./second or more, and still more preferably 2.5° C./second or more. If the cooling rate in a range of TL to 650° C. is excessively increased, supercooled structures such as martensite and bainite are likely to be formed. Therefore, the cooling rate at TL to 650° C. is preferably 5° C./second or less, more preferably 4.5° C./second or less, and still more preferably 4° C./second or less.
(iii) Average cooling rate in a range of 650 to 400° C.: 2° C./second or less
Further, a cooling rate in a range of 650 to 400° C., at which formation of supercooled structures is initiated, is preferably decreased. An average cooling rate in a range of 650 to 400° C. is preferably 2° C./second or less, more preferably 1.5° C./second or less, and still more preferably 1° C./second or less. The lower limit of the average cooling rate is not particularly limited and is, for example, about 0.3° C./second.
To manufacture a coil spring used in automobiles, there is a need that a wire is manufactured by wire processing of the rolled material mentioned above, namely, wire drawing. For example, in a cold coiled spring, quenching and tempering such as high frequency induction heating are performed after wire drawing, and such a wire is also included in the present invention. For example, the rolled material is subjected to wire drawing at an area reduction rate of about 5 to 35%, followed by quenching at about 900 to 1,000° C. and further tempering at about 300 to 520° C. The quenching temperature is preferably 900° C. or higher so as to sufficiently perform austenitizing, and preferably 1,000° C. or lower so as to prevent grain coarsening. The heating temperature for tempering may be set at an appropriate temperature in a range of 300 to 520° C. according to a target value of a wire strength. When quenching and tempering are performed by high frequency induction heating, quenching and tempering times are respectively in a range of about 10 to 60 seconds.
The thus obtained wire of the present invention can realize a high tensile strength in a range of 1,900 MPa or more. The tensile strength is preferably 1,950 MPa or more, and more preferably 2,000 MPa or more. The upper limit of the tensile strength is not particularly limited and is about 2,500 MPa. The wire of the present invention can exhibit corrosion fatigue properties even at a high strength in a range of 1,900 MPa or more because of use of the rolled material of the present invention.
This application claims priority based on Japanese Patent Application No. 2013-272569 filed on Dec. 27, 2013 in Japan, the disclosure of which is incorporated by reference herein.
The present invention will be described in more detail below by way of Examples. It should be noted that, however, these examples are never construed to limit the scope of the invention; various modifications and changes may be made without departing from the scope and spirit of the invention and should be considered to be within the scope of the invention.
Each of steel materials having chemical compositions shown in Tables 1 to 3 was melted by melting in converter and then subjecting to continuous casting and a homogenizing treatment at 1,100° C. or higher. After the homogenizing treatment, blooming was performed, followed by heating at 1,100 to 1,280° C. and further hot rolling to obtain a wire rod having a diameter of 14.3 mm, namely, a rolled material. Whether or not a degassing treatment of a molten steel is implemented, coiling temperature TL after hot rolling, and cooling conditions after cooling are as shown in Tables 4 to 6. In test examples in which “Implementation” is written in the column of the homogenizing treatment, the homogenizing treatment is performed at 1,100° C. for 10 hours or more. In test examples in which the mark “-” is written, the time of the homogenizing treatment at 1,100° C. is less than 10 hours.
With respect to the thus obtained wire rods, namely, rolled materials, the structure was identified by the procedure below, and the amount of nondiffusible hydrogen was measured and also wire drawability was measured.
A cross section of each rolled material was subjected to buffing and etched with an etching solution, and then a microstructure was observed by an optical microscope and each area ratio of a ferrite structure, and bainite and martensite structures (hereinafter, bainite and martensite structures are collectively referred to as supercooled structures) was measured. The measurement was performed at the position of 1 mm deep from a surface. The observation field has a size of 400 μm×300 μm and the measurement was performed with respect to five visual fields, and the average was regarded as a ratio of each structure. The ratio of the pearlite structure was determined by subtracting the ratios of ferrite and supercooled structures from 100%.
A specimen measuring 20 mm in width×40 mm in length was cut out from the rolled material. After raising the temperature of the specimen at a temperature rise rate of 100° C./hour, a hydrogen release amount at 300 to 600° C. was measured using a gas chromatogram, and the hydrogen release amount was regarded as the amount of nondiffusible hydrogen.
Wire drawability was evaluated by reduction of area of a tensile test. A JIS No. 14 specimen was cut out from the rolled material and a tensile test was performed under the conditions of a crosshead speed of 10 mm/minute in accordance with JIS 22241 (2011) using a universal tester, and then reduction of area RA was measured
Next, the rolled material was subjected to wire drawing, namely, cold drawing to obtain a wire having a diameter of 12.5 mm, followed by quenching and tempering. An area reduction rate of the drawn wire mentioned above is about 23.6% and the conditions of quenching and tempering are as follows.
With respect to the wire after wire drawing, and quenching and tempering, the tensile strength, hydrogen embrittlement resistance and corrosion resistance were evaluated.
After quenching and tempering, a wire was cut into a predetermined length and a tensile test was performed at a distance between chucks of 200 mm and a tensile speed 5 mm/minute in accordance with JIS Z2241 (2011)
A specimen measuring 10 mm in width×1.5 mm in thickness×65 mm in length was cut out from the wire after quenching and tempering. In a state where stress of 1,400 MPa is applied to the specimen by four-point bending, the specimen was immersed in a mixed solution of 0.5 mol/L of sulfuric acid and 0.01 mol/L of potassium thiocyanate. Using a potentiostat, a voltage of −700 mV, which is less nobler than that of a saturated calomel electrode (SCE), was applied and the fracture time required for the occurrence of cracking was measured.
A specimen measuring 10 mm in diameter×100 mm in length was cut out from the wire after quenching and tempering by cutting. The specimen was subjected to a salt spray test with an aqueous 5% NaCl solution for 8 hours and then held in a wet atmosphere at 35° C. and a relative humidity of 60% for 16 hours. After repeating this cycle seven times in total, a difference in weight before and after the test was measured and the thus obtained difference was regarded as a corrosion weight loss.
The results (1) to (6) mentioned above are shown in Tables 4 to 6.
Samples of test Nos. 1 to 4, 7 to 11, 15 to 18, 21 to 25, 33, 34, 37 to 40, 45 to 47, 49 to 53, 55 to 60, and 65 to 81 are manufactured from a steel having appropriately adjusted chemical composition under preferred manufacturing conditions mentioned above, so that the amount of nondiffusible hydrogen, and the area ratio of ferrite and supercooled structures satisfy the requirements of the present invention. Therefore, the rolled material exhibits a reduction of area RA of 30% or more in the tensile test and is excellent in wire drawability, and the wire obtained by wire drawing of the rolled material, followed by quenching and tempering has an excellent tensile strength in a range of 1,900 MPa or more. Further, the wire obtained after quenching and tempering exhibits a fracture time of 1,000 seconds or more in an evaluation test of hydrogen embrittlement resistance and a corrosion weight loss of 5.0 g or less in an evaluation test of corrosion resistance, so that the wire is excellent in both hydrogen embrittlement resistance and corrosion resistance. Further, “reduction rate” in Tables 4 to 6 is a value in which a ratio of a difference between a value of right side of the inequality expression (1) and an actual value of a ferrite area ratio to a value of right side of the inequality expression (1) is expressed as percentage.
In contrast, in examples other than the above-mentioned ones, at least any one of the requirements, including the chemical composition of a steel, the amount of nondiffusible hydrogen, the ferrite area ratio, and the supercooled structure area ratio does not satisfy the requirements of the present invention, leading to the result that at least any one property of wire drawability of a rolled material, tensile strength, hydrogen embrittlement resistance, and corrosion resistance of a wire is inferior.
All of samples of test Nos. 5, 6, 19 and 20 are not subjected to the above-mentioned treatment for reduction of nondiffusible hydrogen, so that the amount of nondiffusible hydrogen in the rolled material increased, thus degrading wire drawability.
In samples of tests Nos. 12 and 26, because of low average cooling rate in a range of a coiling temperature TL to 650° C., the ferrite area ratio increased, thus degrading hydrogen embrittlement resistance. In samples of tests Nos. 13 and 27, because of high average cooling rate in a range of a coiling temperature TL to 650° C., the supercooled structures increased, thus degrading wire drawability. In samples of tests Nos. 14 and 28, because of high average cooling rate in a range of 650 to 400° C., the supercooled structure increased, thus degrading wire drawability.
In samples of tests Nos. 29 to 31, the supercooled structure increased, thus degrading wire drawability. In sample of test No. 32, because of a small amount of C, the wire exhibited poor tensile strength. In sample of test No. 35, because of a large amount of C, residual austenite was generated, thus degrading hydrogen embrittlement resistance. In sample of test No. 36, because of a small amount of Si, the wire exhibited poor tensile strength.
In sample of test No. 41, because of a large amount of Mn, toughness was degraded, thus degrading hydrogen embrittlement resistance. In sample of test No. 42, because of a large amount of Panda large amount of S, grain boundary embrittlement occurred, thus degrading hydrogen embrittlement resistance. In sample of test No. 43, because of a large amount of S. grain boundary embrittlement occurred, thus degrading hydrogen embrittlement resistance. In sample of test No. 44, neither Cu nor Ni is not added, thus degrading corrosion resistance.
In sample of test No. 48, Ni is not added, occurred, thus degrading corrosion resistance. In sample of test No. 54, because of a large amount of Cr, dissolving residue of cementite, is which chromium-based carbide and metallic Cr in high concentration are solid-soluted, was generated as a stress concentration source, thus degrading hydrogen embrittlement resistance.
In samples of tests Nos. 61 to 64, because of low average cooling rate in a range of a coiling temperature TL to 650° C., the ferrite area ratio increased, thus degrading hydrogen embrittlement resistance.
The rolled material and the wire of the present invention are industrially useful since they can be suitably used for coil springs that are used in automobiles, for example, a valve spring, a suspension spring and the like that are used in the engine, suspension, and the like.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2013-272569 | Dec 2013 | JP | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/JP14/82728 | 12/10/2014 | WO | 00 |
