US20120291927A1 - Drawn heat treated steel wire for high strength spring use and pre-drawn steel wire for high strength spring use - Google Patents

Drawn heat treated steel wire for high strength spring use and pre-drawn steel wire for high strength spring use Download PDF

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US20120291927A1
US20120291927A1 US13/574,175 US201113574175A US2012291927A1 US 20120291927 A1 US20120291927 A1 US 20120291927A1 US 201113574175 A US201113574175 A US 201113574175A US 2012291927 A1 US2012291927 A1 US 2012291927A1
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steel wire
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Masayuki Hashimura
Tetsushi Chida
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Nippon Steel Corp
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/02—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for springs
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to drawn heat treated steel wire for high strength spring use which can be used as a material for high strength springs produced by cold coiling and to pre-drawn steel wire.
  • the springs which are used for automobile engines, clutches, etc. are being required to offer more advanced performance and higher durability in order to deal with the trend toward lighter weights and higher performances of automobiles. For this reason, their materials, that is, drawn heat treated steel wire for high strength spring use, are also being required to offer high material strength.
  • the material of the drawn heat treated steel wire for high strength spring use is quenched and tempered to impart higher material strength in the drawn heat treated steel wire for high strength spring use, then is cold coiled to obtain a coil spring shape. Furthermore, stress-relief annealing or other heat treatment and nitriding are performed to obtain a finished coil spring.
  • drawn heat treated steel wire for high strength spring use is required to have not only high strength, but also to have a high enough workability that it will not break at the cold coiling and to suppress softening due to the annealing, nitriding, and other heat treatment performed after coiling, that is, to have temper softening resistance.
  • a spring is required to have fatigue characteristics, so drawn heat treated steel wire for high strength spring use is used as a material and further nitrided or shot peened to raise the hardness of the surface layer of the spring.
  • the durability of a spring includes fatigue characteristics and a sag property.
  • the fatigue characteristics are affected by the surface layer hardness.
  • the sag property (property of the spring ending up plastically deforming in the load direction during use) is greatly affected by not only the surface layer hardness, but also the hardness of the base material of the spring. For this reason, in steel wire for high strength spring use, the surface layer hardness after nitriding and the temper softening resistance at the inside where nitrogen is not introduced by nitriding are important.
  • the drawn heat treated steel wire for high strength spring use can be reduced in prior austenite grain size, so a spring with excellent fracture characteristics can be obtained.
  • drawn heat treated steel wire for high strength spring use becomes higher in strength, in cold coiling, breakage may occur and the spring shape may not be able to be formed.
  • some of the inventors proposed drawn heat treated steel wire for high strength spring use obtained by controlling the carbides, making the prior austenite finer, and achieving both strength and cold coiling ability (PLT 1). Furthermore, they proposed drawn heat treated steel wire for high strength spring use obtained by controlling the residual austenite and carbides, refining the prior austenite, and achieving both strength and cold coiling ability (PLT 2 to PLT 4).
  • PHT 1 the initial austenite and carbides
  • PLT 4 both strength and cold coiling ability
  • the starting points of fracture caused by the formation of coarse oxides and carbides are suppressed and the distribution of fine carbides of cementite required for securing strength is made uniform so as to suppress deterioration of the fatigue characteristics and workability of the drawn heat treated steel wire for high strength spring use.
  • PLT 2 focuses on the fact that the region of sparse spherical carbides with a circle equivalent diameter of 2 ⁇ m or more in the region of a sparse distribution of fine spherical carbides (in particular, cementite) affects the dynamic characteristics and defines that region.
  • PLT 3 and PLT 4 take note of the effect of precipitation of fine carbides due to the addition of the alloy element V and limits the nitrogen (N) content to suppress undissolved spherical carbides. That is, they utilize the effect of precipitation of carbides, nitrides, and carbonitrides of V to enable utilization for hardening the steel wire at the tempering temperature or hardening the surface layer in nitriding. Furthermore, there is also an effect on suppressing coarsening of the austenite grain size due to the formation of precipitates. The effect of addition of V is remarkable. However, undissolved carbides or nitride easily form, so even if suppressing the nitrogen (N), the control of precipitation has to be performed precisely.
  • PLT 4 quantitatively compares the undissolved spherical carbides and the precipitated carbides and defines the amounts so as to obtain as much precipitated V carbides, which are effective for the final spring performance, as possible. Specifically, it proposes to weigh the residue of V carbides in the electrolytic solution at a constant potential and compare this with the amount of V which passes through the filter (amount of precipitated V).
  • the above conventional drawn heat treated steel wire for high strength spring use secures a certain extent of uniform dispersion of fine carbides for improving the fatigue characteristics and workability.
  • further uniform dispersion is necessary.
  • the addition of V proposed in PLT 3 and PLT 4 does indeed have the effect of hardening the steel wire at the tempering temperature, hardening the surface layer in nitriding, and refining the austenite.
  • control of the nitrogen (N) content is not easy. As a result, coarse carbides, nitrides, and carbonitrides are precipitated and cause degradation in the fatigue strength.
  • PLT 3 adds Nb and Ti with the aim of the effect of trapping excess nitrogen (N). However, even if doing this, control to a suitable amount of N content is still not easy.
  • PLT 4 samples the residue of undissolved spherical carbides obtained as a result and compares it with the dissolved carbides. Therefore, it does not proactively control uniform dispersion of fine carbides.
  • the present invention has as its object to keep to a minimum the addition of V and other alloy elements, that is, without precisely controlling the N content, develop drawn heat treated steel wire for high strength spring use which has excellent yield strength and hardness and excellent workability and which has superior surface layer hardness and internal hardness even after nitriding.
  • the size of the undissolved spherical carbides in the steel should be small.
  • the effective size is preferably 0.1 ⁇ m or less. If over 1 ⁇ m, the contribution to strength and workability is lost and the deformation characteristics are just degraded. For this reason, the density of presence of undissolved spherical carbides with a circle equivalent diameter of 0.2 ⁇ m or more becomes an important indicator. Therefore, the present invention has as its object the development of steel wire for high strength spring use not allowing the presence of undissolved spherical carbides with a circle equivalent diameter of 0.2 ⁇ m or more.
  • Undissolved spherical carbides are present in the steel material just after casting and become causes of not only poor coiling ability, but also breakage in rolling and drawing. For this reason, to prevent a detrimental effect in the steps of blooming after casting, wire rod rollingwire rod, patenting, quenching, and drawing, it is effective to raise the heating temperature in each step and constantly suppress undissolved spherical carbides.
  • the undissolved spherical carbides are mainly cementite (Fe 3 C).
  • the undissolved spherical carbides often include Cr, V, etc. It is learned that not only are Cr, V, and other alloy elements wastefully consumed, but there is also a possibility of degrading the mechanical characteristics after nitriding (surface hardness, internal hardness, etc.)
  • undissolved spherical carbides means undissolved carbides with a ratio of the maximum size (long size) and minimum size (short size) (aspect ratio) of 2 or less.
  • carbides and spherical carbides are also undissolved.
  • these respectively are also called “undissolved carbides” and “undissolved spherical carbides”.
  • the present invention was made based on these discoveries.
  • the gist of the invention is as follows:
  • Drawn heat treated steel wire for high strength spring use as set forth in any one of (3) to (6) characterized said drawn heat treated steel wire for high strength spring use has a a surface Vicker's hardness of HV750 or more and an internal Vicker's hardness of HV570 or more aftersoft nitriding of keeping at 500° C. for 1 hour.
  • a method of production of pre-drawn steel wire for high strength spring use characterized by taking a bloom containing, by mass %, C: 0.67% or greater and less than 0.9%,
  • a method of production of heat treated steel wire for high strength spring use characterized by drawing said pre-drawn steel wire which was produced by the method of production of pre-drawn steel wire as set forth in any one of (8) to (10), heating by a heating rate of 10° C./sec or more up to an A 3 point, holding at a temperature of the A 3 point or more for 1 minute to 5 minutes, then cooling by a cooling rate of 50° C./sec or more down to 100° C. or less.
  • a method of production of heat treated steel wire for high strength spring use as set forth in (11) characterized by further holding and tempering it at 400 to 500° C. for 15 minutes or less.
  • FIG. 1 is a micrograph of the metal structure showing one example of spherical carbides in the drawn heat treated steel wire for high strength spring use of the present invention. At the tips of the arrows in the figure, undissolved spherical carbides are observed.
  • FIG. 2 is a view showing the shape of a punch for providing a notch in a test piece.
  • FIG. 3 is a view showing the step of providing a notch in a test piece.
  • FIG. 4 is a view showing an outline of a notch bending test.
  • FIG. 5 is a view showing a method of measurement of a notch bending angle.
  • a wire rod for a spring is produced as follows:
  • production of springs is not limited to this here described process. This is described as just one example.
  • a bloom made of steel containing predetermined chemical compositions is rolled to obtain a billet.
  • the billet is rolled to produce a predetermined diameter of steel wire.
  • the steel wire which is produced at this stage is called the “pre-drawn steel wire”.
  • the steel wire which is produced after rolling is patented and drawn to obtain further finer steel wire, then the working stress at the surface layer is removed and subsequent cold coiling workability is obtained by heat treatment (quenching and tempering).
  • the steel wire which is produced at this stage is called the “drawn heat treated steel wire”.
  • the spring is worked by cold coiling and is improved in strength and surface hardness by nitriding. In this way, a “spring” is produced as a final product.
  • the chemical compositions of the drawn heat treated steel wire for high strength spring use of the present invention and its material, that is, pre-drawn steel wire for high strength spring use, will be explained.
  • the “%” in the chemical compositions means mass % except when otherwise indicated.
  • the lower limit of the amount of C is made 0.67% or more.
  • the amount of C is preferably made 0.70% or more, more preferably 0.75% or more.
  • the upper limit of the amount of C is made less than 0.9%. From the viewpoint of suppressing the formation of spherical carbides, the upper limit of the amount of C is preferably 0.85%, more preferably 0.80%.
  • Si is an important element for improving the temper softening resistance of the steel and the sag property of the spring. To obtain these effects, 2.0% or more has to be added. Further, Si is effective for spheroidization and refinement of the cementite. To suppress the formation of coarse spherical carbides, 2.1% or more of Si is preferably added. To raise the internal hardness after nitriding and other treatment for making the surface layer harder, 2.2% or more of Si is more preferably added. Furthermore, from the balance with Cr, Si is more preferably made 2.3% or more. Si is sometimes made 3.0% or more.
  • the upper limit of the amount of Si is made 3.5% or less. From the viewpoint of the prevention of embrittlement, the upper limit is preferably made 3.4%, more preferably 3.3% or less.
  • Mn is an element which is important for raising the quenchability and stably securing the amount of residual austenite.
  • Mn has to be added in 0.5% or more, more preferably 0.65% or more, still more preferably 0.70% or more.
  • the upper limit of the amount of Mn is made 1.2% or less, preferably 1.1% or less, more preferably 1.0% or less.
  • Cr is an element which is effective for improving the quenchability and temper softening resistance. To obtain these effects, 1.3% or more of Cr has to be added.
  • N is an element, in the present invention, which forms nitrides with Al etc. included as impurities in the steel. To utilize the fine nitrides and refine the prior austenite, 0.003% or more of N has to be included. On the other hand, if the amount of N is excessive, the nitrides coarsen and the cold coiling ability and fatigue characteristics fall. Therefore, the upper limit of the amount of N is made 0.007% or less. Further, if considering the ease of heat treatment etc., the amount of N is preferably 0.005% or less.
  • P is an impurity. It causes the steel to harden, forms segregation, and causes embrittlement, so the upper limit of the amount of P is made 0.025% or less. Further, the P which segregates at the prior austenite grain boundaries causes the toughness and delayed fracture resistance etc. to fall, so the upper limit of the amount of P is preferably made 0.015% or less. Furthermore, when the yield strength of the steel wire will exceed 2150 MPa, the amount of P is preferably limited to less than 0.010%.
  • the upper limit of the amount of S is made 0.025% or less.
  • MnS is an inclusion.
  • the upper limit of the amount of S is preferably made 0.015% or less.
  • the amount of S is preferably limited to less than 0.01%.
  • the amount of Al becomes less than 0.0005%, silica-based hard oxides are easily formed. For this reason, the amount of Al is made 0.0005% or more.
  • the lower limit of the amount of Al is preferably 0.0007%, more preferably 0.0008%, further preferably 0.001% or more.
  • the amount of Si exceeds the prescribed amount, the embrittlement becomes extreme and the workability in coiling is impaired. Not only that, decarburization in the intermediate processes becomes remarkable. For this reason, in the final product of the spring, the surface layer hardness becomes lower and the durability falls. Further, decarburized parts are randomly formed, so the stability of the strength of the spring product is impaired. When the amount of Si is smaller than the prescribed amount, the strength falls. Furthermore, the sag property is insufficient. This appears in the hardness after nitriding as well. Sufficient hardness cannot be secured both at the surface layer and inside.
  • Si is an element which destabilizes cementite. If adding a large amount of Cr or other element which stabilizes cementite, in heating, there is the effect of promoting the formation of a solid solution by the cementite. Therefore, regardless of adding a large amount of Cr, if the amount of addition of Si is small, the amount of undissolved spherical carbides becomes greater and the workability is remarkably reduced.
  • the inventors discovered that it is possible to use the difference between the Si content (mass %) and Cr content (mass %) in the steel, that is, the Si ⁇ Cr amount, as a yardstick.
  • Si ⁇ Cr when the value of Si ⁇ Cr is smaller than 0.3%, the amount of Cr becomes relatively large and undissolved spherical carbides easily remain. On the other hand, if over 1.2%, Si becomes relatively excessive and easily causes embrittlement, decarburization, or other problems. Therefore, the value of Si ⁇ Cr should be made 0.3 to 1.2%.
  • the lower limit is preferably 0.35 ⁇ Si ⁇ Cr, more preferably 0.4 ⁇ Si ⁇ Cr.
  • V is an element which forms nitrides, carbides, and carbonitrides. Fine V nitrides, carbides, and carbonitrides with a circle equivalent diameter of less than 0.2 ⁇ m are effective for refinement of the prior austenite. Further, they may also be utilized for hardening the surface layer by nitriding. However, on the other hand, undissolved carbides and nitrides are easily formed, so even if suppressing the nitrogen (N), it is necessary to precisely control the precipitation.
  • V is not deliberately added.
  • V should be added in 0.03% or more, preferably 0.035% or more, more preferably 0.04% or more.
  • the V content should be made 0.1% or less.
  • the upper limit of the amount of V is preferably made 0.09% or less, more preferably 0.08% or less, most preferably 0.05% or less.
  • the amount of addition of V is preferably made 0.05% or less.
  • V is an element which greatly affects the formation of residual austenite in the same way as Mn, so the amount of V has to be precisely controlled together with the amount of Mn.
  • Nb is an element which forms nitrides, carbides, and carbonitrides in steel. These precipitates are sometimes used for control of the austenite grain size etc. However, simultaneously, excessive addition reduces the ductility when hot and results in easier cracking in rolling or hot forging. For this reason, excessive addition must be avoided.
  • Nb is added for the purpose of controlling the amount of N.
  • the precipitates are not directly used for controlling the quality.
  • Valve springs and other springs are produced by quenching, tempering, then cold coiling, but at that time, the dissolved nitrogen obstructs color deformation and reduces the limit strain. For this reason, the coiling ability is impaired. Therefore, by adding Nb and forming nitrides at a high temperature, there is the effect that the dissolved nitrogen in the steel in the steel matrix is lowered and the cold workability is improved.
  • V is an element which is effective for improving the temper softening resistance in nitriding and the surfacemost layer hardness.
  • V nitrides, V carbides, and V carbonitrides often are not sufficiently dissolved.
  • the undissolved spherical carbides of V grow from cores of the V-based nitrides formed at the time of normal high temperature.
  • V was not made an essential element.
  • Nb forms nitrides at a higher temperature than V. For this reason, in the steelmaking process, addition of Nb suppresses the formation of V nitrides. That is, Nb forms nitrides in the high temperature region where V dissolves and does not form nitride. Furthermore, at the high temperature where V nitrides are formed, Nb consumes nitrogen, so V nitrides become harder to form even when cooled. For this reason, the addition of a fine amount of Nb is particularly effective for suppressing undissolved spherical carbides and securing coiling ability when adding a large amount of V.
  • the amount of addition of Nb is made 0.015% or less, preferably 0.010% or less, more preferably 0.005% or less, most preferably less than 0.001%.
  • the effect of Nb in controlling the amount of N in spring steel appears starting from 0.0005%, so when adding Nb, 0.0005% or more is preferably added. Further, when adding V etc., addition of a fine amount of Nb is more effective. A range of 0.003 to 0.012% is preferable. Furthermore, a range of 0.005 to 0.009% is more preferable. The effect is obtained even at 0.005 to 0.001%.
  • V is not deliberately added.
  • addition of a fine amount of V has an effect on the refinement of the prior austenite and formation of residual austenite.
  • Cr and V are both elements which prevent softening upon the heating by the annealing or nitriding etc. performed after the spring coiling, that is, impart so-called temper softening resistance.
  • nitriding causes nitrides to precipitate at the nitrided part of the surface layer to thereby improve the surface hardness and increase the nitriding effect. Further, even at the inside where nitriding does not spread, decomposition of the carbides is suppressed. Further, there is the effect of suppressing softening by precipitation of carbides.
  • both are elements which facilitate the formation of undissolved spherical carbides.
  • V also has a dissolution temperature of the precipitates higher than the A3 point of steel, so easily remains as undissolved spherical carbides.
  • Cr+V is preferably 1.4% or more. Furthermore, 1.5% or more is preferable.
  • the Cr+V is preferably 2% or less, more preferably 1.8% or less.
  • Mn and V are elements which improve the quenchability and also have a large effect on the formation of residual austenite. If Mn is larger than the prescribed amount, a large amount of residual austenite remains. Therefore, the sum of both Mn and the V which is included as an unavoidable impurity has a direct effect on the austenite behavior. If these exceed their prescribed amounts, the amount of residual austenite increases. Not only is the workability affected, but also the yield strength is greatly affected. Sufficiently durability cannot be secured.
  • the total of the contents of Mn and V that is, Mn+V
  • Mn+V the total of the contents of Mn and V, that is, Mn+V
  • the lower limit of Mn+V has to be made 0.7% or more.
  • transformation induced plasticity causes the ductility to be improved and enables the cold coiling ability to be secured.
  • the upper limit value of Mn+V has to be made 1.3% or less. Due to this, the formation of work-induced martensite due to strike marks in cold coiling is suppressed and local embrittlement can be prevented.
  • Mo is an element which improves the quenchability. Further, it is also extremely effective for improving the temper softening resistance. In the present invention, in particular, to further improve the temper softening resistance, 0.05% or more of Mo can be added. Further, Mo is an element which forms Mo-based carbides in the steel. The temperature at which the Mo-based carbides precipitate is lower than carbides of V etc. For this reason, addition of a suitable amount of No is also effective for suppressing coarsening of carbides. Addition of 0.10% or more of Mo is preferable. On the other hand, if the amount of addition of Mo is over 0.30%, a supercooled structure easily forms in hot rolling, the patenting before drawing, etc.
  • the upper limit of the amount of Mo is made 0.30% or less, preferably 0.25% or less. Further, if the amount of Mo is large, in the patenting, the time until the end of the pearlite transformation becomes longer, so the amount of Mo is preferably made 0.20% or less. Furthermore, to shorten the patenting time and stably end the pearlite transformation, 0.15% or less is preferable.
  • W is an element which is effective for improvement of the quenchability and temper softening resistance and is an element which precipitates in the steel as carbides.
  • 0.05% or more of W is added to improve the temper softening resistance.
  • the amount of W is preferably 0.1 to 0.2%, more preferably 0.13 to 0.18%.
  • Mo and W are elements which are effective for improvement of the temper softening resistance. If adding the two combined, the growth of carbides is suppressed and the temper softening resistance can be remarkably improved compared with addition of Mo and W alone. In particular, to improve the temper softening resistance in heating to 500° C., Mo+W has to be made 0.05% or more, preferably 0.15% or more.
  • Mo+W is over 0.5%
  • the upper limit of Mo+W is made 0.5% or less, preferably 0.35% or less.
  • Mg forms oxides in molten steel higher in temperature than the MnS forming temperature. At the time of formation of MnS, it is already present in the molten steel. Therefore, it can be used as a nuclei for precipitation of MnS. Due to this, the distribution of the MnS can be controlled. Further, in number distribution as well, Mg-based oxides are more finely dispersed in the molten steel compared with the Si- and Al-based oxides which are often seen in conventional steel, so MnS formed around cores of Mg-based oxides are finely dispersed in the steel. Therefore, even with the same S content, depending on the presence of Mg, the MnS distribution differs. Adding these makes the MnS grain size finer.
  • MnS finely disperse
  • the upper limit of the amount of addition of Mg was made 0.002%, preferably 0.0015% or less.
  • the amount of addition of S is suppressed, so if considering the yield etc., 0.001% or less is preferable.
  • Mg has the effect of improving the corrosion resistance and resistance to delayed fracture preventing rolling cracks due to the effect of the distribution of MnS etc. Addition of as much as possible is preferable, so control of the amount of addition in the extremely narrow range of 0.0002 to 0.001% is preferable.
  • Ca is an oxide- and sulfide-forming element.
  • spring steel it makes the MnS spherical to thereby suppress the length of MnS serving as initiation sites of fatigue and other fracture and render it harmless.
  • the effect is similar to Mg.
  • Addition of 0.0002% or more is preferable. Further, even if over 0.002% is added, not only is the yield poor, but also oxides and CaS and other sulfides are formed and trouble in production and degradation in spring fatigue durability characteristics are caused, so the amount was made 0.002% or less.
  • the amount of addition when used for a high strength valve spring, the inclusion susceptibility is high, so the amount is preferably 0.0015% or less, more preferably 0.001% or less.
  • Zr is an oxide-, sulfide-, and nitride-forming element.
  • the oxides are finely dispersed, so like with Mg, form nuclei for precipitation of MnS and can make the MnS finely disperse. Due to this, it is possible to improve the fatigue durability and, further, increase the ductility to thereby improve the coiling ability.
  • 0.0002% or more is preferably added. Further, even if over 0.003% is added, not only is the yield poor, but oxides and ZrN, ZrS, and other nitrides and sulfides are formed and trouble in production or degradation in the spring fatigue durability characteristics is caused, so the amount is made 0.003% or less.
  • the amount of addition is preferably 0.0025% or less. Furthermore, when used for high strength valve spring, there is also the effect that the coiling ability is improved by the control of sulfides, so addition is preferred, but to minimize the effects on the dimensions of inclusions, suppression to 0.0015% or less is preferable.
  • Undissolved spherical carbides perform the important role of securing strength in steel wire for high strength spring use.
  • the presence of undissolved spherical carbides causes the coiling ability to deteriorate. Further, coarse carbides cause the fatigue characteristics to degrade as well. Therefore, suppressing undissolved spherical carbides in coiling and causing uniform dispersion of fine carbides after the final nitriding are essential for solving the problem of the present invention.
  • the steel wire for high strength spring use of the present invention has a long size of the undissolved spherical carbides of 0.2 ⁇ m or less, that is, is suppressed in coarsening.
  • the undissolved spherical carbides are already present after wire rod rolling (that is, the pre-drawn steel wire).
  • the undissolved spherical carbides are hard to go into solid-solution in the subsequent heat treatment (patenting, generation of working heat in drawing, and quenching and tempering, for instance). Rather, they sometimes grow in these heat treatment steps and coarsen. That is, the undissolved spherical carbides in the pre-drawn steel wire sometimes act as nuclei for coarsening of themselves.
  • the steel wire for high strength spring use of the present invention is increased in strength by having C added, having Mn and Cr added and, further having Mo, W, and other so-called alloy elements added.
  • C and Mn and Cr added and, further having Mo, W, and other so-called alloy elements added.
  • Cr and other alloy elements which form nitrides, carbides, and carbonitrides
  • spherical cementite carbides and alloy-based carbides easily remain in the steel.
  • Spherical cementite carbides and alloy-based carbides are undissolved spherical carbides which do not dissolve in the steel in heating in the hot rolling.
  • spherical alloy-based carbides and spherical cementite carbides will be referred to all together as spherical carbides.
  • spherical carbides In the steel, there are pin-shaped carbides corresponding to the pin-shaped structure of tempered martensite, but these pin-shaped carbides are not included in the spherical carbides of the present invention.
  • the pin-shaped carbides are not present right after quenching and precipitate in the process of tempering.
  • the tempered martensite structure is a structure suitable for achieving both strength and toughness and workability. Being pin-shaped is, in a certain sense, the ideal form in carbides.
  • the undissolved spherical carbides can be observed under a scanning electron microscope (SEM) by polishing a sample obtained from pre-drawn steel wire or drawn heat treated steel wire for high strength spring use to a mirror finish and etching it by picral or electrolytically etching it. Further, they can be observed by the replica method under a transmission type electron microscope (TEM).
  • SEM scanning electron microscope
  • FIG. 1 shows an example of a structural photograph of a sample after electrolytic etching as observed under an SEM.
  • the steel is observed to have two types of structures of the matrix, that is, pin-shaped structures and spherical structures.
  • the pin-shaped structures are tempered martensite formed by quenching and tempering.
  • the spherical structures are carbides 1 made spherical by not dissolving into the steel due to the heating of the hot rolling and by being made spherical by quenching and tempering by oil tempering or induction hardening treatment (undissolved spherical carbides). Spherical carbides can be observed at the front end of the arrow in FIG. 1 .
  • the undissolved spherical carbides affect the characteristics of the drawn heat treated steel wire for high strength spring use, so are controlled in size as follows: Note that, in the present invention, compared with the prior art, further finer spherical carbides are defined for achieving both higher performance and workability. Spherical carbides with a circle equivalent diameter of less than 0.2 ⁇ m are extremely effective for securing the strength and temper softening resistance of the steel.
  • spherical carbides with a circle equivalent diameter of 0.2 ⁇ m or more do not contribute to improvement of the strength or temper softening resistance and degrade the cold coiling ability.
  • the present invention is characterized by not allowing the formation of spherical carbides with a circle equivalent diameter of 0.2 ⁇ m or more.
  • the pre-drawn steel wire and drawn heat treated steel wire of the present invention is characterized in that the undissolved spherical carbides have a circle equivalent diameter of less than 0.2 ⁇ m. For this reason, it is possible to secure strength while securing workability as well.
  • the pre-drawn steel wire has to be then patented, drawn and heated, quenched and tempered, or otherwise heat treated, so the undissolved spherical carbides may grow and coarsen.
  • the circle equivalent diameter of the undissolved spherical carbides in the pre-drawn steel wire is preferably made smaller than 0.2 ⁇ m.
  • the circle equivalent diameter of undissolved carbides of the pre-drawn steel wire is confirmed to be able to be reduced to 0.18 ⁇ m or less. Further, it is also confirmed that if making the billet heating temperature 1250° C. or more, the diameter can be made 0.15 ⁇ m or less.
  • the surface of the sample is corroded by electrolytic action in an electrolytic solution (a mixture of acetyl acetone 10 mass %, tetramethyl ammonium chloride 1 mass %, and a balance of methyl alcohol) using the sample as the anode and platinum as the cathode using a current generator with a lower potential.
  • the potential becomes constant at a potential suitable for the sample in the range of ⁇ 50 to ⁇ 200 mV vs SCE.
  • the amount of power run can be found by the total surface area of the sample ⁇ 0.133 [c/cm 2 ]. Note that, when embedding the sample in a resin, not only the polished surface, but also the area of the sample surface in the resin are added to the total surface area of the sample. The power starts to be run, then the sample is held for 10 seconds, then the power is stopped and the sample is cleaned.
  • the sample is observed under an SEM and a structural photograph of the spherical carbides is taken.
  • the structures which appear relatively white and which have a ratio (aspect ratio) of the maximum size (long size) and minimum size (short size) of 2 or less are the spherical carbides.
  • the magnification of the photograph taken under the SEM is X1000 or more, while X5000 to X20000 is preferable.
  • 10 fields were randomly selected from locations at a depth of about 0.5 to 1 mm from the surface of the wire rod while avoiding the center segregation parts.
  • the thus captured SEM structural photographs were processed by image processing to measure the minimum size (short size) and maximum size (long size) of the spherical carbides seen in the measured fields and calculate the circle equivalent diameter.
  • the circle equivalent diameter is the diameter when calculating the area of an undissolved carbide in a field by image processing and converting it to a circle of the same area. Further, it is also possible to measure the density of presence of spherical carbides with a circle equivalent diameter of 0.2 ⁇ m or more seen in the measurement field.
  • the metal structure of the drawn heat treated steel wire for high strength spring use according to the present invention is comprised of, by volume rate, over 6% to 15% of residual austenite and a balance of tempered martensite. Fine inclusions are allowed.
  • the “fine inclusion” are oxides and sulfides. The oxides are deoxidation products of Al and Si etc., while the sulfides correspond to MnS, CaS, etc. Further, the balance of the tempered martensite structure also includes undissolved spherical carbides in fine amounts.
  • the prior austenite grain size number in the structure is #10 or more, while the circle equivalent diameter of the spherical carbides is less than 0.2 ⁇ m.
  • the pearlite structure accounts for 90% or more, preferably 95% or more, more preferably 98% or more.
  • a substantially 100% pearlite structure is ideal.
  • the drawn heat treated steel wire for high strength spring use of the present invention is mainly comprised of tempered martensite in structure.
  • the prior austenite grain size has a great effect on the characteristics. That is, if refining the grain size of the prior austenite, due to the effect of grain refinement, the fatigue characteristics and the coiling ability are improved. In the present invention, to obtain sufficient fatigue characteristics and coiling ability, the prior austenite grain size number is made #10.
  • the prior austenite grain size number is preferably made #11, more preferably #12. To refine the grain size of prior austenite, it is effective to lower the heating temperature of the quenching. Note that, the “prior austenite grain size number” is based on JIS G 0551. If actually performing the quenching by lowering the heating temperature and shortening the time, the prior austenite grain size can be refined, but unreasonable low temperature, short time treatment not only increases the undissolved spherical carbides, but also sometimes results in insufficient austenite transformation itself and two-phase quenching. Conversely, sometimes the coiling ability and the fatigue characteristics are lowered. For this reason usually #13.5 is the upper limit.
  • the microstructure at the drawn heat treated steel wire for high strength spring use after quenching and tempering is comprised of tempered martensite, residual austenite, and a slight volume fraction of inclusions (here, precipitates also expressed included in inclusions). Residual austenite is effective for improving the cold coiling ability.
  • the volume rate of the residual austenite is made over 6%, preferably 7% or more, more preferably 8% or more.
  • the volume rate of the residual austenite is made 15% or less, preferably 14% or less, more preferably 12% or less.
  • the volume rate of the residual austenite can be found by the X-ray diffraction method and the magnetic measurement method.
  • the magnetic measurement method enables simple measurement of the volume rate of the residual austenite, so is the preferable measurement method.
  • the volume rate is measured, but the obtained figures are the same as the area rate.
  • residual austenite is softer than tempered martensite, so reduces the yield strength. Further, the transformation induced plasticity is used to improve the ductility, so this remarkably contributes to improvement of the cold coiling ability. On the other hand, residual austenite often remains at the segregated parts, prior austenite grain boundaries, and near regions sandwiched by the sag grains, so the martensite which is formed by the work-induced transformation (work-induced martensite) becomes starting points of fracture. Further, if the residual austenite increases, the tempered martensite falls relatively.
  • a spring is required to have a superior fatigue strength.
  • a high strength spring is produced by bending the material of the drawn heat treated steel wire for high strength spring use to a desired shape, then nitriding, shot peening, or otherwise hardening the surface. In the nitriding, the spring is heated to 500° C. or so, so the spring is sometimes softened more than the material of the drawn heat treated steel wire for high strength spring use.
  • the drawn heat treated steel wire for high strength spring use is high in yield strength, it is possible to improve the fatigue characteristics and sag property of the spring hardened at the surface by nitriding etc.
  • the yield strength of the drawn heat treated steel wire for high strength spring use is made 2100 MPa or more.
  • the drawn heat treated steel wire for high strength spring use has a yield strength of preferably 2200 MPa or more, more preferably 2250 MPa or more.
  • the yield strength is made 2400 MPa or less.
  • the yield strength or yield point of the drawn heat treated steel wire for high strength spring use means the top yield strength when a yield point is seen at the stress-strain curve in a single-axis tensile test and the 0.2% proof stress when no yield point is seen.
  • raising the yield strength is preferable.
  • raising the yield strength of the spring raising the yield strength of the material, that is, the drawn heat treated steel wire for high strength spring use, is preferable.
  • the drawn heat treated steel wire for high strength spring use preferably has a yield strength of 1600 MPa or more for securing the strength and sag property of the spring.
  • the yield strength is preferably made 1980 MPa or less. Note that to raise the yield strength of the drawn heat treated steel wire for high strength spring use of the material having the same yield strength right after short time quenching and tempering, it is preferable to lower the volume the volume rate of the residual austenite.
  • a high strength spring is improved in surface layer hardness in nitriding, but the inside softens.
  • the conventional heating temperature becomes 500° C., it was difficult to suppress softening at the inside of the drawn heat treated steel wire for high strength spring use.
  • the drawn heat treated steel wire for high strength spring use of the present invention is excellent in temper softening resistance and enables fatigue characteristics and the sag property of the spring after heating at 500° C. to be secured.
  • the surface layer hardness and the internal hardness after gas soft nitriding are defined.
  • the surface layer hardness is made a micro Vicker's hardness at the depth of 50 to 100 ⁇ m from the surface layer of 750 or more. If less than 750, the surface layer hardness becomes insufficient and the fatigue durability also becomes inferior, so residual stress after shot peening cannot be sufficiently imparted.
  • the surface layer hardness is 780 or more.
  • the Vicker's hardness is sometimes measured when, in quenching, the temperature of the surface layer of the steel wire is higher than the inside, so measuring this at a position of 500 ⁇ m depth from the surface is preferable.
  • the Vicker's hardness after heat treatment holding the wire at 500° C. for 1 hour should be 570 or more. Furthermore, 575 or more is preferable.
  • the upper limit of the Vicker's hardness after holding at 500° C. for 1 hour for heat treatment is not particularly defined, but to ensure that the Vicker's hardness before the heat treatment is not exceeded, usually it is made 783 or less.
  • the surface layer is hardened by shot peening, nitriding, etc.
  • the Vicker's hardness at a position of 500 ⁇ m depth from the surface of the high strength spring is affected by the heating in nitriding. Therefore, when actually producing a spring, the internal hardness will fluctuate depending on the temperature of the nitriding.
  • the chemical compositions, spherical carbides, and prior austenite crystal grain size are believed to be little affected by the cold coiling and nitriding. Therefore, the chemical compositions, spherical carbides, and prior austenite crystal grain size of the high strength steel made using the drawn heat treated steel wire for high strength spring use of the present invention as a material are the same extent as the chemical compositions, spherical carbides, and prior austenite crystal grain size of the drawn heat treated steel wire for high strength spring use of the present invention.
  • a steel bloom adjusted to predetermined chemical compositions was rolled to produce a steel billet reduced in size. Further, the billet was heated, then hot rolled to obtain pre-drawn steel wire for high strength spring use. This pre-drawn steel wire for high strength spring use was patented, the shaped and, furthermore, was annealed for softening the hard layer. It was then drawn, quenched, and tempered to produce drawn heat treated steel wire for high strength spring use.
  • the “patenting” is heat treatment for making the structure of the steel wire after hot rolling ferrite and pearlite and is performed for softening the steel wire before drawing. After drawing, oil tempering, induction hardening treatment, and other quenching and tempering are performed to adjust the steel wire in structure and characteristics.
  • the process of preventing coarsening of the spherical carbides is important.
  • the bloom or billet after casting is made a heating temperature of 1250° C. or more. Due to this, it is possible to make the undissolved spherical carbides sufficiently dissolve. For this reason, in the heating of the subsequent rolling, patenting, and quenching, the heating temperature and the heating time are insufficient, so undissolved spherical carbides easily remain, but to enable sufficient dissolution from the start, the dimensions of the undissolved spherical carbides can be controlled to less than 0.2 ⁇ m.
  • the bloom heating temperature should be 1270° C. or more.
  • the hot rolling is preferably completed within 5 minutes.
  • the heating temperature before rolling of the bloom should be made 1250° C. or more, more preferably 1270° C. or more.
  • the rolling step of heating before drawing it is important to make the bloom heating temperature and the billets heating temperature sufficiently high for the carbides to dissolve. Due to this, the size of the undissolved spherical carbides can be kept small.
  • the rolling of the spring steel is completed in several minutes from extraction of the billet from the heating furnace to a size of material before drawing of about ⁇ 10 mm. For this reason, it is important to heat to 1200° C. or more where the effect of the billet heating temperature is the largest. 1250° C. or more is more preferable. 1270° C. or more is more preferable.
  • the wire After rolling, the wire is taken up in a coil and air cooled at that time as general practice. For this reason, usually the microstructure of the pre-drawn steel wire (steel wire after rolling of wire rod) is comprised of ferrite and pearlite or pearlite with a high pearlite structure fraction since the amount of C is high. Undissolved spherical carbides are present in the base material.
  • the undissolved spherical carbides can be observed by observing a polished and etched detection sample by an SEM.
  • the undissolved carbides can be clearly differentiated from the lamellar cementite contained in the pearlite structure of the base material since they are spherical.
  • the magnitude may also be measured.
  • the pre-drawn steel wire for spring use is patented.
  • the heating temperature of this patenting may be made 900° C. or more to promote dissolution of the carbides. A high temperature of 930° C. or more is more preferable. Further, 950° C. or more is preferable. After that, the wire may be patented at 600° C. or less.
  • the method of patenting and drawing is not limited. If a general patenting and drawing method for steel wire, the same treatment as usual may be performed.
  • the patenting step before the drawing may be omitted.
  • the heating temperature in the later explained quenching high (for example, 970° C. or more)
  • dissolution of the undissolved spherical carbides is promoted.
  • the quenching after the drawing is performed by heating to temperature of the A 3 point or more.
  • the heating rate is preferably made 10° C./sec or more and the holding time at the temperature of the A 3 point or more is preferably made 1 minute to 5 minutes.
  • the cooling rate is preferably made 50° C./sec to 100° C.
  • the coolant in the quenching process is preferably made 100° C. or less, more preferably a low temperature of 80° C. or less, but in the present invention, to precisely control the amount of residual austenite, the coolant temperature is made 40° C. or more.
  • the coolant is not particularly limited so long as being an oil, a water soluble quenching agent, water, or other coolant which enables quenching.
  • the cooling time may be shortened like with oil tempering and induction hardening treatment. It is preferable to avoid extending the holding time at a low temperature for greatly reducing the residual austenite and lowering the coolant temperature to 30° C. or less. That is, the quenching is preferably ended within 5 minutes.
  • tempering After quenching, tempering is performed.
  • the tempering suppresses the growth of carbides, so it is preferable to make the heating rate 10° C./sec or more and make the holding time 15 minutes or less.
  • the holding time fluctuates due to the chemical compositions and the targeted strength, but the material is usually held at 400 to 500° C.
  • the pre-drawn steel wire for high strength spring use is cold coiled to work it to the desired spring shape, is relieved of stress, and is nitrided and shot peened to produce the spring.
  • the cold coiled steel wire is reheated by stress-relieving annealing, nitriding, etc. At this time, the inside is softened, so the performance of the spring falls.
  • the pre-drawn steel wire for high strength spring use of the present invention as a material, it is possible to make the micro Vicker's hardness at a depth of 500 ⁇ m from the surface layer of high strength springs HV575 or more. Note that, the micro Vicker's hardness is measured at a depth of 500 ⁇ m from the surface layer of the spring so as to evaluate the Vicker's hardness of the base material not affected by nitriding and shot peening for hardening.
  • a diameter 8 mm pre-drawn steel wire (rolled wire rod) is preferably made an easily drawn structure by patenting it before drawing.
  • the heating temperature at the patenting is preferably 900° C. or more so that the carbides etc. sufficiently dissolve.
  • the patenting is performed by heating at 930° C., then charging the sample into a 600° C. flowing bed. After patenting, the wire is drawn to obtain a diameter 4 mm drawn wire rod. In this way, by heating the bloom at a high temperature, then making the temperature in the rolling process, patenting, and quenching as high as possible, it is possible to suppress growth of undissolved spherical carbides and keep the dimensions down to 0.2 ⁇ m or less.
  • the wire was quenched and tempered to produce pre-drawn steel wire for spring use. Note that, a sample which broke in the drawing was not quenched and tempered.
  • the quenching and tempering were performed by heating the drawn steel wire by a 10° C./sec or more heating rate at 950° C. or 1100° C. (temperature of A 3 point or more), holding at the peak heating temperature for 4 minutes to 5 minutes, then placing the steel in a room temperature water tank so that the cooling rate became 50° C./sec or more and cooling down to 100° C. or less.
  • the target values to be passed were made as follows with reference to conventional steel wire for high strength spring use.
  • Prior austenite grain size number 10 degrees or more
  • Residual austenite amount (vol %): 20% or less
  • Circle equivalent diameter of spherical carbides 0.2 ⁇ m or less
  • Notch bending angle 28 degrees or more
  • Average fatigue strength (Nakamura type rotating bending strength): 900 MPa or more
  • Nitrided layer hardness by Vicker's hardness after gas nitriding 750 Hv or more
  • a sample was taken from the obtained drawn heat treated steel wire for spring use, evaluated for prior austenite grain size, volume rate of residual austenite, and carbides, then was subjected to a tensile test, notch bending test, and micro Vicker's hardness test.
  • the fatigue characteristics were evaluated by treatment simulating production of a spring (below, referred to as “spring production and treatment”) including gas nitriding simulating nitriding performed on the spring after working (500° C., 60 minutes), shot peening (diameter of cut wire 0.6 mm, 20 minutes), and low temperature stress-relieving treatment (180° C., 20 minutes).
  • the prior austenite grain size number was measured based on JIS G 0551 .
  • the circle equivalent diameter and density of presence of the carbides were measured by using an electrolytically etched sample, obtaining a SEM structural photograph, and analyzing the image. Further, the volume rate of the residual austenite was measured by the magnetic measurement method.
  • the fatigue test is a Nakamura type rotating bending fatigue test (fatigue test bending by two-point supported weight and turning by motor to apply compressive and tensile stress to surface of wire).
  • the maximum load force of 10 samples showing a lifetime of 10 7 cycles or more by a probability of 50% or more was made the average fatigue strength.
  • the notch bending test is a test for evaluating the cold coiling ability and is performed as follows.
  • a punch 2 with an angle of the tip shown in FIG. 2 of 120° was used to provide a groove (notch) of a maximum depth of 30 ⁇ m in the test piece.
  • the notch 4 was provided at a right angle to the longitudinal direction at the center of the test piece 3 in the longitudinal direction.
  • a pusher 5 was used to apply a load P of a maximum tensile stress through a load-use fixture 6 and the test piece was deformed by three-point bending.
  • D is the diameter of the test piece.
  • notch bending angle The bending angle at the time of fracture (notch bending angle) was measured as shown in FIG. 5 . Note that, when the test piece was split, the fractured parts were placed together to measure the notch bending angle ⁇ . In the present invention, a sample with a notch bending angle of 28° or more is judged to be excellent in cold coiling ability.
  • the micro Vicker's hardness after nitriding was evaluated using the depth of 500 ⁇ m or more from the surface layer as the internal hardness was defining the micro Vicker's hardness of a depth of 50 ⁇ m from the surface layer as the “nitrided layer hardness”.
  • the measurement weight was 10 g.
  • Tables 1-5 to 1-8 The results of these tests are shown in Tables 1-5 to 1-8. Note that, in Tables 1-5 to 1-8, the metal structure is comprised of residual austenite ( ⁇ ) plus tempered martensite and slight inclusions. Further, the balance of the chemical compositions was iron and unavoidable impurities.
  • the pre-drawn steel wire (steel wire after rolling wire rod) was evaluated only by the circle equivalent diameter of the undissolved spherical carbides. This is because since this is before heat treatment, even if measuring the mechanical properties or the austenite grain size etc., there is not much meaning to the figures.
  • Examples 1 to 47 of the present invention all have the indicator of the cold coiling ability, that is, the notch bending angle, of a good 28° or more and have an excellent indicator of the spring durability, that is, the Nakamura type rotating bending fatigue strength (hereinafter simply referred to as the “fatigue durability”) and an excellent indicator of the sag property and temper softening resistance, that is, the nitrided layer hardness.
  • Comparative Examples 48 and 49 are examples where the amount of addition of C is outside the range of the claims. If C is over the prescribed amount (Comparative Example 48), the undissolved spherical carbides become greater and the indicator of the cold coiling ability, the notch bending angle, is low. On the other hand, if C is smaller than the prescribed amount (Comparative Example 49), a sufficient yield strength cannot be secured. In particular, the internal hardness after nitriding becomes lower and the spring fatigue durability (Nakamura type rotating bending fatigue strength) and the sag property (internal hardness after nitriding).
  • Comparative Examples 50 and 51 are examples where the amount of addition of Si is outside the range of the claims. If Si exceeds the prescribed amount, the matrix is embrittled and the workability is impaired, that is, the notch bending angle is low. On the other hand, if Si is smaller than the prescribed amount, the quenching and tempering characteristics deteriorate, so sufficient strength cannot be secured after heating by nitriding. In particular, the internal hardness after nitriding and the nitrided layer hardness become low.
  • Comparative Examples 52 and 53 are examples where the amount of addition of Mn is outside the range of the claims. If Mn is over the prescribed range, the residual austenite becomes greater, the yield strength falls, and the fatigue durability (Nakamura type rotating bending fatigue strength) is inferior. On the other hand, when Mn is smaller than the prescribed amount, the residual austenite falls too much and the workability deteriorates, so the notch bending angle falls.
  • Comparative Examples 54 and 55 are examples where the amount of addition of Cr is outside the range of the claims. If the Cr is over the prescribed range, cementite stabilizes and even in the high temperature heating of the bloom or billet, quenching and tempering, etc., undissolved carbides increase and the spring workability is greatly reduced. For this reason, the notch bending angle falls. On the other hand, if Cr is smaller than the prescribed amount, the steel ends up softening in the heat treatment in the nitriding etc. and the so-called temper softening resistance otherwise becomes insufficiently so the nitrided layer hardness falls.
  • Comparative Examples 56, 57, and 58 are examples where the amounts of addition of Mo, W, and Mo+W are over the ranges of the claims. If Mo and W exceed the prescribed amounts, in rolling and cooling and after patenting and other heat treatment, a supercooled structure of martensite, bainite, etc. forms, the wire breaks in the conveyance or drawing process, and the measurement test cannot be performed.
  • Comparative Example 59 is an example of excessive addition of V.
  • V is an element which forms carbides in the steel. Excessive addition causes undissolved carbides to form around the V, the workability to deteriorate, and the notch bending angle to fall.
  • Comparative Examples 60 and 61 are cases where the amount of N is excessive compared with the range of the claims. This excessive N raises the temperature of formation of nitrides and carbonitrides of V, Nb, etc. and causes coarsening of carbides and other precipitates using these as nuclei. Further, when used for repeated heating such as in the present invention, the nitrides, carbonitride, and carbides are incompletely dissolved and a large amount of coarse undissolved spherical carbides remain. As a result, the workability is impaired. This is an example where the notch bending angle falls.
  • Comparative Examples 62 and 63 are examples where the amount of addition of Nb is outside the range of the claims. If Nb exceeds the prescribed amount, the hot ductility is remarkably impaired, numerous surface flaws occur at the rolled material, wire breakage occurs during drawing, and a measurement test could not be run.
  • Comparative Examples 64 is the case where the sum of the amounts of addition of Mn and V is more than the range explained in the present invention.
  • the amount of residual austenite in the steel wire becomes greater than the prescribed value.
  • the notch part hardens due to the stress-induced transformation and the workability falls. This is an example where the notch bending angle falls. While repeating our, V is not added in the present invention, but sometimes V is included as an unavoidable impurity, so this is a limitation for rendering the V harmless.
  • Comparative Examples 65 is the case where the sum of the amounts of addition of Mn and V is lower than the range explained in the present invention.
  • the amount of residual austenite is smaller than the optimum range, so the workability, that is, the notch bending angle, falls.
  • Comparative Example 66 is the case where the sum of the amounts of addition of Cr and V is greater than the scope explained in the present invention.
  • the undissolved spherical carbides excessively remain and the workability, that is, the notch bending angle, falls.
  • Comparative Example 67 is the case where the sum of the amounts of addition of Cr and V is less than the range explained in the present invention.
  • the workability is excellent, but the internal hardness after nitriding and the nitrided layer hardness are insufficient and the spring performance is not sufficient.
  • Comparative Examples 68 to 70 are cases where the difference between the amount of Si and the amount of Cr ([Si %]-[Cr %]) is off from the scope of the claims and the amount of Cr is greater than the amount of Si. If Cr is excessive with respect to the amount of Si, undissolved spherical carbides remain and the workability is degraded, that is, that is, the notch bending angle falls.
  • Comparative Examples 71 and 72 are the case where the difference of the amount of Si and the amount of Cr ([Si %]-[Cr %]) is larger than the upper limit of the range of the claims. Si is very excessive compared with the amount of Cr. In these cases, the surface layer decarburized layer of the rolled material greatly grows and cannot be sufficiently removed by a slight amount of surface layer shaving. For this reason, the fatigue durability (Nakamura type rotating bending fatigue strength) was inferior.
  • Comparative Examples 73 and 74 are respectively the Invention Example 1 and Invention Example 23 where the steel is rolled at the billet heating temperature 1100° C. At the start of the rolling, undissolved spherical carbides remain. The effects finally remain, so the workability is degraded, that is, the notch bending angle falls.
  • Invention Examples 101 to 109 are examples of the pre-drawn steel wires of Invention Examples 1 to 5 and 20 to 23.
  • Comparative Examples 110 and 111 are the Invention Examples 101 and 106 where the billet heating temperature is made 1100° C.
  • the pre-drawn steel wire is evaluated, so only the maximum circle equivalent diameter of the undissolved spherical carbides is evaluated. If the billet heating temperature is high, it is learned that the circle equivalent diameter of the undissolved spherical carbides becomes smaller.
  • the present invention can be utilized for the production of steel wire for high strength spring use.
  • the high strength spring material can be utilized in many industrial fields starting from the automotive industry.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Heat Treatment Of Articles (AREA)
  • Springs (AREA)
  • Metal Extraction Processes (AREA)
US13/574,175 2010-07-06 2011-07-05 Drawn heat treated steel wire for high strength spring use and pre-drawn steel wire for high strength spring use Abandoned US20120291927A1 (en)

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JP2010-154030 2010-07-06
PCT/JP2011/065749 WO2012005373A1 (ja) 2010-07-06 2011-07-05 高強度ばね用伸線熱処理鋼線および高強度ばね用伸線前鋼線

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US20170130303A1 (en) * 2014-07-01 2017-05-11 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Wire rod for steel wire, and steel wire
US10689726B2 (en) 2014-09-04 2020-06-23 ThyssenKrupp Federn und Stabilisatoren GmbH Method for producing hot-formed steel springs
WO2020233872A1 (en) * 2019-05-20 2020-11-26 Nv Bekaert Sa Method of making a spring core for a mattress or for seating products
CN113416834A (zh) * 2021-01-26 2021-09-21 陈冬英 一种钢丝热处理淬火工艺
US20220307115A1 (en) * 2019-07-01 2022-09-29 Sumitomo Electric Industries, Ltd. Steel wire and spring
SE2151318A1 (en) * 2021-10-28 2023-04-29 Suzuki Garphyttan Ab Flat wire and method for production thereof

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JP6453138B2 (ja) * 2015-03-31 2019-01-16 株式会社神戸製鋼所 曲げ加工性に優れた熱処理鋼線
WO2018211779A1 (ja) * 2017-05-19 2018-11-22 住友電気工業株式会社 オイルテンパー線
WO2019010661A1 (zh) * 2017-07-13 2019-01-17 田圣林 一种高韧性高强度耐腐蚀弹簧
CN111448328B (zh) * 2018-03-29 2022-05-24 日本制铁株式会社 热冲压成形体
MX2021008968A (es) * 2019-02-26 2021-08-24 Bekaert Sa Nv Resorte de compresion helicoidal para un accionador para abrir y cerrar una puerta o compuerta trasera de un automovil.
CN115298338B (zh) * 2020-02-21 2024-04-02 日本制铁株式会社 钢线
CN112427484B (zh) * 2020-11-11 2022-07-26 南京工程学院 一种再结晶退火调控不锈弹簧钢线成形制造方法
KR102492641B1 (ko) * 2020-12-17 2023-01-30 주식회사 포스코 내피로특성과 질화처리 특성이 향상된 스프링용 선재, 강선, 스프링 및 그 제조 방법
KR20220163153A (ko) * 2021-06-02 2022-12-09 주식회사 포스코 강도 및 피로한도가 향상된 스프링용 선재, 강선, 스프링 및 그 제조방법

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Cited By (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20170130303A1 (en) * 2014-07-01 2017-05-11 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Wire rod for steel wire, and steel wire
US10689726B2 (en) 2014-09-04 2020-06-23 ThyssenKrupp Federn und Stabilisatoren GmbH Method for producing hot-formed steel springs
WO2020233872A1 (en) * 2019-05-20 2020-11-26 Nv Bekaert Sa Method of making a spring core for a mattress or for seating products
CN113874135A (zh) * 2019-05-20 2021-12-31 贝卡尔特公司 制造用于床垫或就座产品的弹簧芯的方法
US20220307115A1 (en) * 2019-07-01 2022-09-29 Sumitomo Electric Industries, Ltd. Steel wire and spring
CN113416834A (zh) * 2021-01-26 2021-09-21 陈冬英 一种钢丝热处理淬火工艺
SE2151318A1 (en) * 2021-10-28 2023-04-29 Suzuki Garphyttan Ab Flat wire and method for production thereof
WO2023075660A1 (en) * 2021-10-28 2023-05-04 Suzuki Garphyttan Ab Flat wire and method for production thereof
SE545660C2 (en) * 2021-10-28 2023-11-28 Suzuki Garphyttan Ab Flat wire and method for production thereof

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WO2012005373A1 (ja) 2012-01-12
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SE537538C2 (sv) 2015-06-09
CN102482747A (zh) 2012-05-30
JP4980496B2 (ja) 2012-07-18
CN102482747B (zh) 2014-03-05
KR20120040728A (ko) 2012-04-27

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