EP2096186A1 - Automatenstahl mit hervorragender fertigungsfreundlichkeit - Google Patents

Automatenstahl mit hervorragender fertigungsfreundlichkeit Download PDF

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EP2096186A1
EP2096186A1 EP07849980A EP07849980A EP2096186A1 EP 2096186 A1 EP2096186 A1 EP 2096186A1 EP 07849980 A EP07849980 A EP 07849980A EP 07849980 A EP07849980 A EP 07849980A EP 2096186 A1 EP2096186 A1 EP 2096186A1
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EP
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Prior art keywords
machinability
steel
amount
mns
mno
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French (fr)
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EP2096186A4 (de
EP2096186B1 (de
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Masayuki Hashimura
Atsushi Mizuno
Kenichiro Miyamoto
Jun Aoki
Seiji Ito
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Nippon Steel Corp
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Nippon Steel Engineering Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur

Definitions

  • the present invention relates to low carbon machining steel used for automobiles, general machinery, etc. where machinability is required more than strength characteristics, more particularly relates to machining steel superior in tool life at the time of machining, finished surface roughness, chip evacuation, and other machinability, accompanied with little melt loss of plate refractories of the continuous casting sliding nozzles, and superior in manufacturability with good ductility in hot rolling.
  • Japanese Patent Publication (A) No. 11-222646 proposes the method of introducing 30 or more independent sulfides of 20 ⁇ m or more or groups of sulfides of lengths of a plurality of sulfides connected in substantially straight lines of 20 ⁇ m or more in a 1 mm 2 field of the cross-section in the rolling direction so as to improve the chip evacuation.
  • no allusion is made, including of the method of production, of the dispersion of submicron level sulfides most effective for machinability. Further, this cannot be expected from the ingredients either.
  • Japanese Patent Publication (A) No. 9-17840 Japanese Patent Publication (A) No. 2001-329335 , Japanese Patent Publication (A) No. 2002-3991 , and Japanese Patent Publication (A) No. 2000-178683 are art using BN to improve the machinability. However these are not intended for improving the finished surface roughness.
  • Japanese Patent Publication (A) No. 9-17840 Japanese Patent Publication (A) No. 2001-329335 , and Japanese Patent Publication (A) No. 2000-178683
  • the object is the improvement of the tool life, while in Japanese Patent Publication (A) No.
  • the object is the improvement of the chip evacuation.
  • a sufficient effect cannot be obtained in improvement of the finished surface roughness.
  • the matrix is made uniform by the fine dispersion of BN in the steel, the effect of improvement of the finished surface roughness cannot be obtained, but these patent documents do not describe this art.
  • Japanese Patent Publication (A) No. 5-345951 is art improving the machinability by increasing the concentration of oxygen in the steel so as to make the MnS larger in size.
  • the reduction of MnS due to the increase in the oxygen and the accompanying reduction of the machinability are not alluded to at all.
  • measures for preventing melt loss of refractories, increase of surface defects, and other remarkable deterioration of the manufacturability are not touched upon either.
  • Japanese Patent Publication (A) No. 2001-329335 discloses the art of suppressing grain boundary embrittlement due to precipitation of BN at the grain boundaries and furthermore limiting the amount of N added for making use of the action of solid-solute B in preventing grain boundary embrittlement.
  • this only reduces the amount of N.
  • Control of the amount of solid-solute N in the BT heating to work temperature range is not sufficiently considered.
  • the amount of solid-solute N is not sufficiently reduced as required for preventing defects.
  • the amount of N is limited to one lower than the stoichiometric composition, so the amount of BN is insufficient for improving the finished surface roughness. Using other art for making up for this is not considered at all as well, so it is not possible to obtain a good finished surface roughness.
  • Japanese Patent Publication (A) No. 2004-27297 proposes the art of reducing the surface defects by limiting the amount of oxygen in the steel.
  • the method of control of the amount of oxygen in the steel is not alluded to at all.
  • the present invention provides low carbon machining steel used for automobiles, general machinery, etc. particularly machining steel superior in tool life at the time of machining, finished surface roughness, chip evacuation, and other machinability, accompanied with little melt loss of plate refractories of the continuous casting sliding nozzles, and superior in ductility in hot rolling, and able to prevent deterioration of the surface properties due to hot rolling.
  • Machining is a phenomenon of removal of chips. Promoting this is one of the key points. However, as already explained, there are limits with just increasing the S. Further, to achieve both machinability and manufacturability, it is also necessary to consider the amounts of the machinability improving elements.
  • the inventors discovered that by controlling the amount of solid-solute N in the rolling temperature range and controlling the ratio of the amounts of B and N required for obtaining the BN required for machinability at room temperature where machining is performed, it is possible to achieve both hot ductility and machinability.
  • the "solid-solute N” is the total amount of N minus the amount of compound N.
  • the "amount of compound N” substantially shows the amount of N forming BN. This solid-solute N is produced in large amounts since the BN becomes solid solute by heating in the rolling temperature range of 800 to 1100°C. For good rolling with little occurrence of surface defects, it is necessary to reduce the amount of solid-solute N in this temperature range.
  • MnS which is easily consumed as an oxide in the molten steel
  • B the yield of B
  • the present invention was made based on the above discovery and has as its gist the following:
  • the present invention provides low carbon machining steel in which machinability is required more than strength characteristics, which improves the machinability, without adding Pb, by adding B and making it precipitate as BN, wherein, regarding the composition of ingredients of the steel, in particular B and N are added so as to satisfy a suitable relationship to thereby improve the machinability and the ductility at the time of hot rolling and wherein MnO in the steel is reduced so as to improve the machinability and the lifetime of the refractories for control of the amount of injection in continuous casting, whereby the invention is completed. Furthermore, the present invention finely disperses MnS-based inclusions in the steel to improve the machinability. Below, the composition of ingredients prescribed in the present invention and the reasons for limitation will be explained.
  • C is related to the basic strength of the steel material and the amount of oxygen in the steel, so has a large effect on the machinability. If adding a large amount of C to improve the strength, the machinability is reduced, so the upper limit was made 0.2%. On the other hand, if simply using blow refining and overly reducing the amount of C, not only will the costs swell, but also the oxygen will no longer be removed by the C, so a large amount of oxygen will remain in the steel and will cause pinholes and other problems. Therefore, an amount of C of 0.005% able to easily prevent pinholes and other problems was made the lower limit.
  • Mn is required for fixing and dispersing the sulfur in the steel as MnS. Further, it is necessary for softening the oxides in the steel and rendering the oxides harmless. The effect depends on the amount of S added, but if less than 0.3%, the added S is sufficiently fixed as MnS leading to surface defects and S becomes FeS leading to embrittlement. If the amount of Mn becomes large, the hardness of the material also becomes greater and the machinability and cold workability fall, so 3.0% was made the upper limit.
  • Sulfides mainly comprised of MnS improve the machinability, while sulfides mainly comprised of flattened MnS constitute one cause of anisotropy at the time of forging.
  • Large sulfides mainly comprised of MnS should be avoided, but from the viewpoint of the improvement of the machinability, addition of a large amount is preferable. Therefore, causing sulfides mainly comprised of MnS to finely disperse is preferable.
  • addition of 0.30% or more is necessary for improvement of the machinability when not adding Pb.
  • B easily forms oxides, so if the dissolved O in the molten steel is high, it ends up being consumed as oxides and the amount of BN effective for improvement of the machinability is sometimes reduced. Adding Ca to lower the dissolved oxygen (free oxygen) to a certain extent, then adding B to improve the yield of the amount of B substantially becoming BN is effective for improving the machinability.
  • Ca is a deoxidizing element. It can control the amount of dissolved oxygen (free oxygen) in the steel material, stabilizes the yields of the easily oxide forming Mn and B, and furthermore can suppress the formation of hard oxides. Further, if slight in amount, it forms soft oxides and acts to improve the machinability. If less than 0.0001%, this effect is nonexistent, while if over 0.0010%, a large amount of soft oxides are formed and deposit on the tool cutting edges as relief shapes, so the finished surface roughness becomes extremely bad. Not only this, but also a large amount of hard oxides are produced. Furthermore, the machinability and the hot ductility are lowered. Therefore, the range of the ingredient was defined as 0.0001 to 0.0010%.
  • Al is a deoxidizing element and forms Al 2 O 3 or AIN in the steel.
  • Al 2 O 3 is hard, so becomes a cause of tool damage and promotes wear at the time of machining.
  • AIN the amount of N for forming BN ends up being reduced and the machinability falls. Therefore, the amount was made 0.01% or less where Al 2 O 3 and AIN are not produced in large amounts.
  • BN forms inclusions improving the machinability. By finely dispersing them in a high density, the machinability is remarkably improved.
  • BN has solubility with respect to steel. Along with a rise in the steel temperature, its solubility becomes greater and the amount of solid-solute N increases. If the amount of N becoming solid solute in the rolling temperature range (800 to 1100°C) is great, this will become a cause of rolling defects, so it is necessary to limit the amount of solid-solute N to a certain amount or less.
  • the amount of N is less than 0.0020%, the absolute amount of N becomes insufficient and the distance of dispersion to places where B is present in the steel becomes greater, so even with an amount of addition of N of the stoichiometric ratio, sufficient BN cannot be produced. For this reason, it is necessary to secure 0.0020% or more. Due to the above, to achieve both manufacturability and machinability, it is necessary that the N content satisfy N ⁇ 0.020% and 1.3 ⁇ B-0.0100 ⁇ N ⁇ 1.3 ⁇ B+0.0034.
  • Mn is an element strong in affinity with oxygen. Formation of MnO becomes unavoidable in the presence of a certain amount of dissolved oxygen (free oxygen) in the molten steel. MnO is an inclusion with relatively low melting point and softness. It itself does not cause remarkable deterioration of the tool life and other aspects of machinability like a hard inclusion such as Al 2 O 3 . However, if the MnO increases, the amount of Mn forming MnS is reduced and the fine dispersion of the MnS is obstructed, so the machinability deteriorates. Furthermore, in an environment where a large amount of MnO is produced, the dissolved oxygen (free oxygen) in the molten steel becomes a high concentration.
  • the amount of formation of B oxides also increases, the amount of B forming BN is reduced, and the machinability is further degraded. Further, if the Mn forming MnS is reduced, it is no longer possible to fix the S at a high temperature, so a large number of FeS particles are formed and therefore the hot ductility is degraded.
  • the melt loss of the plate refractories of the continuous casting sliding nozzles becomes severer and the manufacturability is remarkably degraded.
  • the area of the MnO in the steel having a circle equivalent diameter of 0.5 ⁇ m or more in the cross-section of the steel material perpendicular to the rolling direction is over 15% of the area of the total Mn-based inclusions, the deterioration of the machinability and manufacturability becomes remarkable, so to obtain good machinability and manufacturability, it is necessary that the MnO in the steel be not more than 15% of the total Mn-based inclusions.
  • MnO is, by circle equivalent diameter, 0.5 ⁇ m or less, its area rate is extremely small, therefore the amount of Mn consumed by the MnO is also slight, so the amount of production of MnS is not greatly affected. For this reason, it is defined as having a circle equivalent diameter of 0.5 ⁇ m or more.
  • MnO is usually present as MnO alone and is also sometimes present bonded with other oxides, but in the present invention, what is measured by the following method is identified as the "MnO" and its area is found.
  • FIG. 3 An example of measurement of the MnO by EPMA is shown in FIG. 3 .
  • a test piece cut out from a position of the steel material at a depth of 1/4 of the diameter of the cross-section perpendicular to the rolling direction, buried in resin, and polished was measured by an electron probe microanalyzer (EPMA) for at least 20 fields, each field being 200 ⁇ m ⁇ 200 ⁇ m.
  • EPMA electron probe microanalyzer
  • the MnO's 13 in the steel of the steel material are present in a state contained in sulfides mainly comprised of MnS 14, so in elemental area analysis by EPMA, the parts where Mn and O overlap are deemed MnO and that area is found.
  • total Mn-based inclusions is the general term for all of the inclusions combined with Mn in the steel. This covers the later explained sulfides mainly comprised of MnS, oxides of MnO alone, and oxides of MnO bonded with other oxides.
  • the total Mn-based inclusions can also be identified by elemental area analysis by EPMA and their area measured, so the ratio of the area of the MnO measured with respect to the area of the total Mn-based inclusions measured is found.
  • Sulfides mainly comprised of MnS are inclusions for improving the machinability. By finely dispersing them at a high density, the machinability is remarkably improved.
  • the presence of surface relief has a great effect on the height of the peaks, that is, the finished surface roughness, but sulfides mainly comprised of MnS dispersed finely at a high density make the steel material uniform and thereby can improve the breaking characteristics of the steel material, reduce the surface relief, and improve the finished surface roughness. This is more effective for improvement of the finished surface roughness of parts such as shafts of office automation equipment machined by longitudinal turning.
  • the dimensions have to be a circle equivalent diameter of 0.1 to 0.5 ⁇ m.
  • the distribution of sulfides mainly comprised of MnS is observed under an optical microscope to measure the dimensions and density.
  • Sulfides mainly comprised of MnS of these dimensions cannot be confirmed by observation by an optical microscope and can only first be observed by a transmission electron microscope (TEM).
  • TEM transmission electron microscope
  • Sulfides mainly comprised of MnS are of dimensions where even if there is no difference in dimensions and density in observation under an optical microscope, clear differences are observed by observation under a TEM. In the present invention, this is controlled and the state of presence is converted into a numerical value so as to differentiate the invention from the prior art.
  • sulfides of less than the minimum diameter of 0.1 ⁇ m do not substantially affect the machinability. Therefore, the density of sulfides mainly comprised of MnS having a circle equivalent diameter of 0.1 to 0.5 ⁇ m was made 10000/mm 2 .
  • the sulfides mainly comprised of MnS form nuclei for precipitation of the Bn which is hard to make uniformly finely disperse in the matrix, whereby the BN can be made to uniformly finely disperse and the effect of improvement of the machinability, in particular the finished surface roughness, by BN can be made more remarkable.
  • the "sulfides mainly comprised of MnS” include not only pure MnS, but also include inclusions of sulfides of Fe, Ca, Ti, Zr, Mg, REM, etc. solid solute with MnS or bonded together for copresence, inclusions such as MnTe where elements other than S form compounds with Mn to become solid solute or bond with MnS for copresence, the above inclusions precipitated with oxides as their nuclei, that is, inclusions able to be expressed by the chemical formula (Mn,X)(S,Y) (where X: sulfide forming elements other than Mn and Y: elements bonding with Mn other than S). This is the general term for Mn sulfide-based inclusions.
  • the cooling rate at the time of casting should be 10 to 100°C/min. This cooling rate can be easily obtained by controlling the size of the casting mold cross-section, the casting speed, etc. to suitable values. This can be applied to both continuous casting and ingot making.
  • the "solidification and cooling rate” referred to here, as shown in FIG. 8 means the speed at the time of cooling from the liquidus temperature to the solidus temperature at the depth position 18 (see FIG. 8(b) ) of 1/4 the thickness (L) of the cast slab in the horizontal cross-section 17 of the cast slab 16 produced by the casting direction 15 shown by the arrow.
  • V forms carbonitrides which can strengthen the steel by secondary precipitation hardening. If less than 0.05%, there is no effect on strengthening, while if added over 1.0%, a large amount of carbonitrides precipitate and conversely the mechanical properties are impaired, so this was made the upper limit.
  • Nb also forms carbonitrides which can strengthen the steel by secondary precipitation hardening. If less than 0.005%, there is no effect on strengthening, while if added over 0.2%, a large amount of carbonitrides precipitate and conversely the mechanical properties are impaired, so this was made the upper limit.
  • Cr is an element improving the hardenability and imparting resistance to tempering softening. Therefore, it is added to steel requiring higher strength. In that case, addition of 0.01% or more is required. However, if adding a large amount, Cr carbides form and cause embrittlement, so 2.0% was made the upper limit.
  • Mo is an element imparting resistance to tempering softening and improving the hardenability. If less than 0.05%, the effect is not recognized, while even if added over 1.0%, the effect becomes saturated, so 0.05% to 1.0% was made the range of addition.
  • W forms carbonitrides which can strengthen the steel by secondary precipitation hardening. If less than 0.05%, there is no effect on strengthening, while if added over 1.0%, a large amount of carbonitrides precipitate and conversely the mechanical properties are impaired, so this was made the upper limit.
  • Ni strengthens the ferrite, improves the ductility, and is also effective for improving the hardenability and improving the corrosion resistance. If less than 0.05%, that effect is not recognized, while even if added over 2.0%, the effect becomes saturated in terms of the mechanical properties, so this was made the upper limit.
  • Cu strengthens the ferrite and is effective for improving the hardenability and improving the corrosion resistance. If less than 0.01%, the effect is not recognized, while even if added over 2.0%, the effect becomes saturated in respect to the mechanical properties, so this was made the upper limit. In particular, the hot ductility is reduced. This easily becomes a cause of defects at the time of rolling. Therefore, addition simultaneously with Ni is preferable.
  • Sn makes the ferrite brittle, extends tool life, and improves the surface roughness as an effect. If less than 0.005%, this effect is not recognized, while even if added over 2.0%, the effect becomes saturated, so this was made the upper limit.
  • Zn makes the ferrite brittle, extends tool life, and improves the surface roughness as an effect. If less than 0.0005%, this effect is not recognized, while even if added over 0.5%, the effect becomes saturated, so this was made the upper limit.
  • Ti is a deoxidizing element which can control the amount of oxygen in the steel and can stabilize the yields of the easily oxide forming Mn and B. Further, if slight in amount, it forms soft oxides and acts to improve the machinability. If less than 0.0005%, this effect is nonexistent, while if over 0.1%, a large amount of hard oxides are formed and the Ti becoming solid solute without forming oxides bonds with N to form hard TiN which lowers the machinability. Therefore, the range of the ingredient was made 0.0005 to 0.1%. Ti forms TiN and thereby consumes the N required for forming BN. Therefore, the amount of addition of Ti is preferably 0.01% or less.
  • Zr is a deoxidizing element which can control the amount of oxygen in the steel and can stabilize the yields of the easily oxide forming Mn and B. Further, if slight in amount, it forms soft oxides and acts to improve the machinability. If less than 0.0005%, this effect is nonexistent, while if over 0.1%, a large amount of soft oxides are formed and deposit on the tool cutting edges as relief shapes, so the finished surface roughness becomes extremely bad. Not only this, but also a large amount of hard oxides are produced. Furthermore, the machinability is lowered. Therefore, the range of the ingredient was defined as 0.0005 to 0.1%.
  • Mg is a deoxidizing element which can control the amount of oxygen in the steel. It can stabilize the yields of easily oxide forming Mn and B. Further, if slight in amount, it forms soft oxides and acts to improve the machinability. If less than 0.0003%, this effect is nonexistent, while if over 0.005%, a large amount of soft oxides are formed and deposit on the tool cutting edges as relief shapes, so the finished surface roughness becomes extremely bad. Not only this, but also a large amount of hard oxides are produced. Furthermore, the machinability is lowered. Therefore, the range of the ingredient was defined as 0.0003 to 0.005%.
  • Te is a machinability improving element. Further, it forms MnTe and, by copresence with MnS, lowers the deformability of MnS to control the flattening of the MnS shapes. Therefore, this element is effective for reducing anisotropy. This effect is not recognized if less than 0.0003%, while even if added over 0.2%, not only does the effect become saturated, but also the hot ductility falls and defects are easily caused.
  • Bi is a machinability improving element. Its effect is not recognized if less than 0.005%, while even if added over 0.5%, not only does the effect of improvement of the machinability become saturated, but also the hot ductility falls and defects are easily caused.
  • Pb is a machinability improving element. Its effect is not recognized if less than 0.005%, while even if added over 0.5%, not only does the effect of improvement of the machinability become saturated, but also the hot ductility falls and defects are easily caused.
  • the 270t converter material was bloomed to a billet, then rolled to ⁇ 9.5. This ⁇ 9.5 mm rolled material was drawn to ⁇ 8 mm and used as the test material. For evaluation of the hot ductility, before the rolling, test pieces were taken from the billet and a 180 mm square cast material. Further, the solidification and cooling rate were adjusted by control of the size of the casting mold cross-section and casting speed.
  • the machinability of the material was evaluated by three typical types of machining methods of a drilling test showing the conditions in Table 7, a plunge cutting test showing the conditions in Table 8, and a longitudinal turning test showing the conditions in Table 9.
  • the drilling test is the method of evaluating the machinability by the highest cutting speed enabling machining up to a cumulative hole depth of 1000 mm, (so-called VL1000, unit: m/min).
  • the plunge cutting test is the method of evaluating the finished surface roughness by transferring the tool shape by a piercing tool of high speed steel (builtup cutting edge shape). A summary of this test method is shown in FIG. 1 . In the test, the finished surface roughness when cutting 200 grooves was measured by a contact type roughness meter.
  • the longitudinal turning test is a machining method cutting into the outer circumference of the steel material of the test piece 2 in the machining direction 3 while feeding the carbide tool 1 in the longitudinal direction. In the same way as plunge cutting, this method repeatedly measures and evaluates the finished surface roughness of the measurement surface 4 of surface roughness in transfer of the tool shape.
  • FIG. 2 A summary of this test method is shown in FIG. 2 . This method performs the test while rotating the test piece 2, feeding the carbide tool 1 along the test piece 2 (0.05 mm/rev), and machining by a predetermined depth of cut 6 (1 mm).
  • Sulfides mainly comprised of MnS finely dispersed at a high density make the steel material uniform and thereby reduce the surface relief and enable a good finished surface roughness, so it is possible to express the effect of the sulfides mainly comprised of MnS dispersed at a high density remarkably well. Further, this method can express the quality of the finished surface roughness resulting from the transfer of tool surface relief due to tool wear after a large amount of machining remarkably well, so in this test, the evaluation was performed using the finished surface roughness after machining 800 pieces - which enables evaluation of the difference of machinability in the state where tool wear has progressed. The finished surface roughness was measured by a contact type roughness meter.
  • the 10-point surface roughness Rz (unit: ⁇ m) was used as an indicator showing the finished surface roughness.
  • G good
  • P Chips with a radius of curvature of over 20 mm, curling continuously by three curls or more, and extending long are poor and were evaluated as "P”.
  • the area rate of MnO of a circle equivalent diameter of 0.5 ⁇ m or more in the cross-section perpendicular to the rolling direction of the steel material was measured by an electron probe microanalyzer (EPMA) using a test piece cut out from a depth position of 1/4 of the diameter of the cross-section perpendicular to the rolling and drawing direction after ⁇ 8 mm drawing, buried in resin, and polished. The measurement was performed for 20 fields or more each of 200 ⁇ m ⁇ 200 ⁇ m. The area rate was found using the area of MnO in the inclusions measured by the elemental area analysis as a ratio with respect to the area of the total Mn-based inclusions.
  • EPMA electron probe microanalyzer
  • the MnO in the steel material is present in a state contained in MnS, so in analysis by EPMA, the area where Mn and O overlap is deemed the area of MnO as differentiated from MnS.
  • the Mn and O were overlaid by image processing.
  • An example of measurement by EPMA is shown in FIG. 3 .
  • the density of sulfides mainly comprised of MnS of dimensions of a circle equivalent diameter of a maximum diameter of 0.5 ⁇ m and a minimum diameter of 0.1 ⁇ m was measured by a transmission electron microscope using a test piece obtained by the extract replica method from a position of a depth of 1/4 the diameter of the cross-section perpendicular to the rolling and drawing direction after ⁇ 8 mm drawing. The measurement was performed at 10000 power for 40 fields or more, each field of 80 ⁇ m 2 . The result was converted to the number of sulfides mainly comprised of MnS per mm 2 .
  • the hot ductility was evaluated by the value of the reduction rate in a high temperature tensile test at 1000°C. If the reduction rate is 50% or more, good rolling is possible, but if less than 80%, numerous surface defects are formed, the area for removal of defects and touchup after rolling becomes greater, and use is not possible for high grade products with severe demands on surface properties. If a value of the reduction rate of 80% or more can be obtained, the formation of surface defects is remarkably reduced, use even without touchup becomes possible, and use for high grade products becomes possible. Furthermore, the touchup costs can also be slashed. Therefore, a reduction rate of 80% or more was evaluated as a "G (good)" hot ductility, while one of less than 80% was evaluated as "P (poor)".
  • the melt loss rate is a value indexing the melt loss rates to the melt loss rate of refractories when the area of MnO of 0.5 ⁇ m or more size constitutes 15% of the total area of Mn-based inclusions as "1". If the melt loss rate exceeds 1, the melt loss of the refractories becomes worse, so a melt loss rate of 1 or less was evaluated as "G (good)" and one over 1 was evaluated as "P (poor)".
  • the invention examples of Examples 1 to 72 were all better than the comparative examples of Examples 73 to 102 in drill tool life and finished surface roughness in plunge cutting and longitudinal turning, had a hot ductility of a value of 80% or more, and enabled good manufacturability with a low melt loss rate.
  • Examples 47, 52, 60, and 62 to 67 to which a slight amount of Pb, known as a free cutting element, is added in Examples 45, 48, 50, 53, 61, 68, and 69 to which a slight amount of Te, also known as a free cutting element, is added, and furthermore in Examples 55 and 70 to 72 to which both Pb and Te are added, it is learned that good hot ductility and machinability are obtained.
  • the comparative examples were all cast by a slow solidification cooling rate, so the density of fine sulfides mainly comprised of MnS becomes smaller and, overall, poor values of machinability, in particular the finished surface roughness by longitudinal turning, are shown.
  • poor values are exhibited since the chemical ingredients are outside the ranges of the present invention.
  • the area rate of MnO is high like in the comparative example of Example 76, the reduction in the amount of MnS and the amount of BN results in a poor value of finished surface roughness.
  • the melt loss rate becomes a large value.
  • Example 80 the MnO area rate of 15% or less is satisfied, but the amounts of S and Ca are outside the invention ranges, so the hot ductility becomes a poor value.
  • the O cannot be control and the large numbers of MnO and hard oxides formed result in poor manufacturability of a hot ductility of less than 80% and a large value of melt loss rate.
  • Examples 90 and 91 are comparative examples with amounts of N below the lower limit. The increase of solid-solute B invites an increase in hardness and a low value of hot ductility is exhibited.
  • Example 93 is a comparative example with amounts of S and N above the upper limits. Due to the increase in solid-solute N, a poor value of hot ductility is exhibited.
  • Example 102 is a comparative example with a high MnO. Poor values of both the finished surface roughness and melt loss index are exhibited.
  • FIG. 4 gives an (a) TEM replica photograph and (b) optical micrograph of sulfides mainly comprised of MnS of an example of the present invention.
  • FIG. 5 gives an (a) TEM replica photograph and (b) optical micrograph of sulfides mainly comprised of MnS of a comparative example of the present invention.
  • FIG. 6 shows changes in machinability due to the MnO area rate using as an example the finished surface roughness by longitudinal turning after machining 800 pieces.
  • Tool wear remarkably progresses at the time of a large amount of machining when the MnO area rate is greater than 15%, so the difference in finished surface roughness, which is governed by the transfer of surface relief due to tool wear, appears remarkably at this as the borderline.
  • FIG. 7 is a view showing a balance of finished surface roughness by longitudinal turning and hot ductility in invention examples and comparative examples.
  • the invention examples are good in finished surface roughness and have a hot ductility of a good region cf 80% or more.
  • the finished surface roughness and the hot ductility are both in the poor range or even if the hot ductility is good, the finished surface roughness is poor.
  • machining steel superior in tool life at the time of machining, finished surface roughness, chip evacuation, and other machinability, accompanied with little melt loss of plate refractories of the continuous casting sliding nozzles, and superior in manufacturability with good ductility in hot rolling.

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  • Organic Chemistry (AREA)
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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3309272A4 (de) * 2015-06-10 2018-10-24 Nippon Steel & Sumitomo Metal Corporation Automatenstahl

Families Citing this family (20)

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Publication number Priority date Publication date Assignee Title
WO2008082153A1 (en) * 2006-12-28 2008-07-10 Posco Eco-friendly pb-free free cutting steel with excellent machinability and hot workability
KR101018091B1 (ko) 2008-07-09 2011-02-25 주식회사 포스코 구성인선이 적고 표면조도가 우수한 무연 쾌삭강 및 그제조방법
JP5488438B2 (ja) * 2010-04-09 2014-05-14 新日鐵住金株式会社 被削性に優れた電縫鋼管
CN102884212A (zh) * 2010-10-06 2013-01-16 新日铁住金株式会社 表面硬化钢及其制造方法
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JP5954484B2 (ja) * 2013-02-18 2016-07-20 新日鐵住金株式会社 鉛快削鋼
WO2014125770A1 (ja) * 2013-02-18 2014-08-21 新日鐵住金株式会社 鉛快削鋼
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KR102471016B1 (ko) * 2018-06-13 2022-11-28 닛테츠 스테인레스 가부시키가이샤 마르텐사이트계 s쾌삭 스테인리스강
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Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2004169052A (ja) * 2002-11-15 2004-06-17 Nippon Steel Corp 被削性に優れる鋼およびその製造方法
JP2004169054A (ja) * 2002-11-15 2004-06-17 Nippon Steel Corp 被削性に優れる鋼
JP2004176177A (ja) * 2002-11-15 2004-06-24 Nippon Steel Corp 被削性に優れる鋼
US20060013720A1 (en) * 2002-11-15 2006-01-19 Masayuki Hashimura Steel superior in machinability and method of production of same

Family Cites Families (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS62149854A (ja) 1985-12-23 1987-07-03 Kobe Steel Ltd 快削鋼の製造方法
KR0150704B1 (ko) 1995-06-29 1998-12-01 김광호 반도체 칩 분리 장치 및 분리방법
JP3437079B2 (ja) 1998-02-05 2003-08-18 株式会社神戸製鋼所 切りくず処理性に優れた機械構造用鋼
JP3687370B2 (ja) 1998-11-25 2005-08-24 住友金属工業株式会社 快削鋼
JP3874557B2 (ja) 1998-12-11 2007-01-31 Ｊｆｅ条鋼株式会社 靱性に優れた快削非調質鋼
JP2001329335A (ja) 2000-05-16 2001-11-27 Kobe Steel Ltd 熱間延性に優れた低炭素硫黄系ｂｎ快削鋼
JP2002003991A (ja) 2000-06-21 2002-01-09 Kawasaki Steel Corp 快削鋼
JP2002249823A (ja) * 2001-02-22 2002-09-06 Kawasaki Steel Corp 快削鋼の製造方法
JP4295959B2 (ja) 2002-06-26 2009-07-15 Ｊｆｅ条鋼株式会社 表面疵の少ない被削性に優れた硫黄および硫黄複合快削鋼
JP4264329B2 (ja) 2002-11-15 2009-05-13 新日本製鐵株式会社 被削性に優れる鋼
JP4348163B2 (ja) * 2002-11-15 2009-10-21 新日本製鐵株式会社 被削性に優れる鋼及びその製造方法
JP4359548B2 (ja) * 2004-09-22 2009-11-04 Ｊｆｅ条鋼株式会社 Ｂｎ系快削鋼
JP4500709B2 (ja) * 2005-03-08 2010-07-14 Ｊｆｅ条鋼株式会社 Ｂｎ快削鋼

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2004169052A (ja) * 2002-11-15 2004-06-17 Nippon Steel Corp 被削性に優れる鋼およびその製造方法
JP2004169054A (ja) * 2002-11-15 2004-06-17 Nippon Steel Corp 被削性に優れる鋼
JP2004176177A (ja) * 2002-11-15 2004-06-24 Nippon Steel Corp 被削性に優れる鋼
US20060013720A1 (en) * 2002-11-15 2006-01-19 Masayuki Hashimura Steel superior in machinability and method of production of same

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of WO2008066194A1 *

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3309272A4 (de) * 2015-06-10 2018-10-24 Nippon Steel & Sumitomo Metal Corporation Automatenstahl

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KR101118852B1 (ko) 2012-03-16
EP2096186A4 (de) 2011-07-13
BRPI0719310A2 (pt) 2014-07-15
EP2096186B1 (de) 2012-10-24
JPWO2008066194A1 (ja) 2010-03-11
TWI363804B (de) 2012-05-11
US20100054984A1 (en) 2010-03-04
AU2007326255A1 (en) 2008-06-05
AU2007326255B2 (en) 2010-06-24
KR20090055648A (ko) 2009-06-02
CN101573463A (zh) 2009-11-04
TW200840875A (en) 2008-10-16
WO2008066194A1 (fr) 2008-06-05
JP5212111B2 (ja) 2013-06-19

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