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EP2305851B1 - Hochfester ungehärteter Stahl für Fracture-Splitting-Verfahren und Stahl-Komponente für Fracture-Splitting-Verfahren - Google Patents

Hochfester ungehärteter Stahl für Fracture-Splitting-Verfahren und Stahl-Komponente für Fracture-Splitting-Verfahren Download PDF

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EP2305851B1
EP2305851B1 EP09803005.9A EP09803005A EP2305851B1 EP 2305851 B1 EP2305851 B1 EP 2305851B1 EP 09803005 A EP09803005 A EP 09803005A EP 2305851 B1 EP2305851 B1 EP 2305851B1
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Prior art keywords
steel
fracture
ferrite
fracture splitting
mass
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English (en)
French (fr)
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EP2305851A4 (de
EP2305851A1 (de
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Hiromasa Takada
Shinya Teramoto
Shinsaku Fukuda
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Isuzu Motors Ltd
Nippon Steel Corp
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Isuzu Motors Ltd
Nippon Steel and Sumitomo Metal Corp
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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
    • 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
    • C22C38/04—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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium

Definitions

  • the present invention relates to a material for a steel part used after fracture splitting, that is, high strength fracture splitting use non-heat treated steel used after hot forging to form a steel part, then immediately applying predetermined cooling, and a fracture splitting use steel part provided with high strength and superior fracture splittability produced using that non-heat treated steel as a material.
  • Non-heat treated steel is steel designed in ingredients so that even as hot forged, then cooled by air cooling or air blast cooling, that is, even omitting the prior quenching and tempering, superior mechanical properties are realized.
  • connecting rod As one part to which non-heat treated steel is broadly applied, there is an engine connecting rod (hereinafter referred to as a "connecting rod”).
  • a connecting rod is consisted of a cap and rod, that is, two parts.
  • the cap and rod were separately fabricated and bolted together.
  • the mating faces of the cap and rod had to be finished to a high precision, so the processing costs rose.
  • Such a fracture split connecting rod enables the step of finishing the mating surfaces to be omitted, so not only are the costs reduced, but also the fracture faces bear part of the stress applied to the connecting rod, so the strength is superior and, accordingly, there are the merits that the bolts and body can be reduced in size.
  • Fracture split connecting rods are widespread in the West. There, the most general fracture splitting use non-heat treated steel is high carbon steel containing about 0.7 mass% of carbon. If using a high carbon composition, the merits are obtained that the ductility deteriorates, so the fracturing work becomes easy and the deformation at the time of fracture becomes smaller, but on the other hand there are the defects that the yield strength and the fatigue strength are inferior.
  • medium carbon (C: 0.30 to 0.60 mass%) is included so as to improve the yield strength. Further, the Mn content and the N content are reduced to realize a high fractureability, that is, a small fracture deformation.
  • Patent Literature 3 discloses, in addition to lowering the Mn and lowering the N, dispersing TiC grains to as to obtain sufficient fracture splittability even with steel having a C content of less than 0.35%.
  • Patent Literature 4 discloses that at the time of hot forging, the pinning of the austenite grains by the TiC is insufficient resulting in mixed grain sizes, so after cooling, the large pearlite grains transform and that this enhances the fracture splittability.
  • Patent Literature 5 discloses a low ductility non-heat treated steel material superior in machineability having Ti carbosulfides or Zr carbosulfides of a maximum size of 10 ⁇ m or less and a total amount of 0.05% or more.
  • Patent Literature 6 discloses applying ferrite-pearlite steel containing C: 0.2 to 0.5% and V: 0.05 to 0.5% and having a ferrite fraction of 20% or less to a fracture split connecting rod.
  • Patent Literature 7 discloses high strength non-heat treated steel suitable for fracture splitting having TiN inclusions in the steel of a maximum size of 5 ⁇ m or more and a density of 5/mm 2 or more and, furthermore, having a pearlite fraction of 20% or more.
  • Patent Literature 8 a method of making the area percentage of pearlite 40% or less and controlling the form of the sulfides to obtain random large surface relief fracture faces is disclosed in Patent Literature 8.
  • Patent Literature 10 discloses making the pearlite fraction 50% or more and, when the carbon content is 0.4 to 0.5%, making P 0.05 to 0.15% is suitable.
  • Patent Literature 11 discloses the method of utilizing Si, V, Ti, P, and solute V to promote brittle fracture and the method of using notches to promote brittle fracture.
  • Patent Literature 12 discloses non-heat treated steel suitable as a material for cranking rods having a ferrite-pearlite structure of a ferrite fraction of 40% or more and, furthermore, having a ferrite hardness of a Vicker's hardness of 250 or more and a ratio of ferrite hardness and overall hardness of 0.80 or more.
  • Patent Literature 14 discloses hot forging use non-heat treated steel enabling easy fracture separation of a forged part after hot forging having a sol-Al, N, and O contents satisfying 0.01[sol-Al%] ⁇ [O%] ⁇ 1.5[sol-Al%], and 0.03[N%] ⁇ [O%] ⁇ 1.6[N%].
  • JP 2005 054 228 discloses a fine grained steel for con-rods having a high strength but also goad rupture separability.
  • the main part covered by the present invention is a high strength connecting rod used after fracture splitting. This is provided with high strength, specifically, 850 MPa or more tensile strength and 650 MPa or more 0.2% proof stress, and realizes superior fractureability.
  • the steel is as low a carbon composition as possible and the part has a ferrite-pearlite structure.
  • bainite easily forms in the hot forged part. If bainite forms, not only does the fractureability deteriorate, but also the yield strength and the yield ratio deteriorate and the mechanical properties necessary for the part can no longer be obtained.
  • a steel material superior in fracture splittability is low in ductility not only at ordinary temperature, but also hot, but also easily is flawed or cracked at the time of production of a steel rod material and at the time of hot forging. Ease of casting and hot rolling of a steel material and hot forging of a part are extremely important requirements industrially.
  • a steel material requires high hot ductility.
  • the problem to be solved by the present invention is to provide high strength non-heat treated steel superior in fracture splittability which is superior in hot ductility and forms a stable ferrite-pearlite structure when hot forged, then cooled by air cooling or air blast cooling, and a fracture splitting use steel part.
  • the present invention was completed based on the above discoveries, so the gist of the present invention is as follows.
  • the high strength fracture splitting use non-heat treated steel of the present invention is superior in hot ductility, forms a stable ferrite-pearlite structure when hot forged, then cooled by air cooling or air blast cooling, and is superior in fracture splittability. Further, a steel part produced from the high strength fracture splitting use non-heat treated steel of the present invention is high in strength, small in amount of deformation at fracture, and superior in fracture splittability and sufficiently provides the hot ductility required at the time of production.
  • FIG. 1 is a view showing a test piece of a shape corresponding to a large end of a connecting rod used for a fracture test. (a) shows the plane state, while (b) shows the side state.
  • Non-heat treated steel for fracture splitting use has already been disclosed in numerous literature. Further, the compositions of ingredients of these steels are widely disclosed. However, in these steels, there are extremely few steels provided with all of the necessary requirements such as (a) superior hot ductility of an extent enabling industrial production, (b) formation of a ferrite-pearlite structure when hot forging, then cooling by air cooling or air blast cooling, (c) high strength, and (d) superior fracture splitting.
  • a ferrite-pearlite structure compared to tempered martensite or a bainite structure, has lower ductility and impact values and has the effect of effectively suppressing deformation at the time of fracture split.
  • the inventors in particular studied the formation of ferrite-pearlite structures when hot rolling, then cooling by air cooling or air blast cooling, and the composition of ingredients exhibiting a superior hot ductility and devised the optimal composition of ingredients as high strength steel for fracture split parts.
  • the first of the features of the steel part of the present invention is it being made of non-heat treated steel positively utilizing V precipitation strengthening.
  • the steel is provided with a ferrite-pearlite structure.
  • a conventional fracture split part often contains a small amount of bainite. This had become a cause of deterioration of the fracture splittability and mechanical properties, but in the present invention, this is improved and a stable quality in industrial production has been achieved.
  • the second of the features is the control of the ferrite volume fraction of the part made by the steel of the present invention to 60% or more, that is, an extremely large value.
  • the deformation at the time of fracture is small and peeling right under the fracture faces and chipping at the final fracture parts are suppressed.
  • the third feature of the present invention is, in addition to the quality as a fracture split part, the improvement of the defect of the "low hot ductility" common to fracture splitting use steel in general.
  • a major problem in ordinary fracture splitting use steel is the cracks and flaws formed at the time of casting and the cracks and flaws formed in the subsequent hot working, that is, hot rolling of the steel rod material and hot rolling of the parts.
  • the experiments were conducted using a hot working reproduction apparatus under the following conditions.
  • the test pieces were made a diameter of 8 mm and a height of 12 mm.
  • the test pieces were heated to 1523K, then were cooled by a 1.0K/s cooling rate, were compressed in the middle of the cooling at 1323K to a height ratio of 60%, and were further cooled by a 1.0K/s cooling rate down to room temperature.
  • test piece was split into two at the center line, the structure of the part at 1/4 thickness of the test piece was observed using an optical microscope, and the presence of any bainite structures was judged.
  • nitric acid alcohol Nital
  • a dilute solution of nitric acid alcohol Nital was used to corrode the structure which was then observed under an optical microscope at a power of 200X and measured for ratio of irregularly shaped ferrite grains.
  • the proeutectoid ferrite grains observed as a ferrite-pearlite structure are white and polygonal in shape, but when irregularly shaped structures which are the same white, but have fine amounts of carbides precipitated in them are discovered, they are judged as bainite.
  • the "irregular shape” basically means a grain shape with relief shapes at the boundaries or shapes changed to pin shapes.
  • the composition when the ratio of the bainite grains in the total number of proeutectoid ferrite grains and bainite grains is less than 3%, the composition is judged to be a ferrite-pearlite structure. If the bainite grains are less than 3%, they have almost no effect on the quality of the material.
  • the lower limit of the K value depends on the lower limits of the different elements, so is not set.
  • the average cooling rate from 1073 to 673K (value obtained by dividing temperature difference of 400K by time elapsed for temperature to fall from 1073K to 673K) is 2.0K/s or less, but to reproduce the structure and hardness of an actual part air cooled by an average cooling rate of 2.0K/s by simple heating and constant speed cooling of a hot working reproduction apparatus, making the average cooling rate after y transformation 1.0K/s is suitable.
  • the material of the test piece among the 68 levels used for finding the above K value, 30 levels in the ranges of C: 0.20 to 0.40% (mass%, same below), Cr: 0.02 to 0.20%, Al: 0.010% or less, Ti: 0 to 0.030%, and Pb: 0.10% or less were used.
  • these plate-shaped materials were cut into lengths of 100 mm, heated to 1503K for 5 minutes, then cooled by blowing air at a rate of 5 m/s down to room temperature.
  • a test piece 1 of a shape simulating the large end of a connecting rod shown in FIG. 1(a) was formed.
  • 45° V-notches 3 having a depth of 1.0 mm and tip curvature of 0.5 mm were formed.
  • a through hole 4 having a diameter of 8.0 mm was formed so that its centerline was at a position 8.0 mm from the side surface at the notched sides.
  • the test relating to fractureability was as follows. That is, the inside diameter of the test piece shown in FIG. 1 was measured, then a split die split in the vertical direction of FIG. 1 was inserted, a shim was inserted into a shim slot formed at the center of the slit die, a 200 kg weight was dropped on the wedge from a 40 mm height, and the test piece was fractured by the impact at the notched position.
  • the split die is on rail. It is structured so that one side is fixed in place, while the other side slides on the rail.
  • the test piece is fastened to the split die by bolts so that the test piece split into two after fracturing will not detach from the split die.
  • the amount of deformation between before and after the test was made the total of the change of the inside diameter. Specifically, after fracturing, the fracture faces were aligned, reconnected, and bolted, then the test piece was measured for inside diameter, the difference from the inside diameter of the initial state measured in advance was found, and the total of the differences in the vertical and lateral directions was made the amount of deformation. It is learned that the smaller the amount of deformation of the inside diameter, the higher the fractureability.
  • the hardness was measured and an optical microscope was used to measure the ferrite volume percentage.
  • the test piece had a shape of a diameter of 8 mm and a height of 12 mm.
  • This test piece heated to 1503K using a hot working reproduction apparatus, then cooled by a cooling rate of 1.0K/s, compressed in the middle of cooling at 1323K by a height ratio of 60%, and further cooled by a cooling rate of 1.0K/s to room temperature.
  • test piece was split into two at the centerline and the structure at the part of 1/4 thickness of the test piece was observed using an optical microscope to investigate the ferrite volume percentage.
  • the F value defined by the following formula (2) is 3.0(%) or less, the result becomes 60% or more.
  • the amount of fracture deformation was a good value equal to or less than the case of using existing non-heat treated steel or fracture splitting use containing 0.7 mass% of C as a material. From this, the F value was limited to 3.0 or less.
  • the amount of ferrite is at a maximum about 75%.
  • F 4.3 ⁇ % C - 0.21 ⁇ % Si + 1.0 ⁇ % Mn + 1.4 ⁇ % Cr - 1.90 ⁇ % P + 1.8 % V - 6.6 ⁇ % N
  • %C, %Si, %Mn, %Cr, %P, %V, and %N are contents in the steel (mass%)
  • the lower limit of the F value depends on the lower limits of the different elements, so is not set.
  • test steels were 96 levels of steel having a composition of ingredients of C: 0.11 to 0.50% (mass%, same below), Si: 0.15 to 1.41%, Mn: 0.17 to 2.46%, P: 0.006 to 0.115%, S: 0.007 to 0.108%, Cr: 0.02 to 1.00%, Al: 0.001 to 0.034%, V: 0 to 0.45%, Ti: 0 to 0.059%, Pb: 0 to 0.260%, Ca: 0 to 0.0041%, and N: 0.0022 to 0.0141%.
  • C 0.11 to 0.50% (mass%, same below)
  • Si 0.15 to 1.41%
  • Mn 0.17 to 2.46%
  • P 0.006 to 0.115%
  • S 0.007 to 0.108%
  • Cr 0.02 to 1.00%
  • Al 0.001 to 0.034%
  • V 0 to 0.45%
  • Ti 0 to 0.059%
  • Pb 0 to 0.260%
  • Ca 0 to 0.0041%
  • N
  • the test piece was made a rod shape of a diameter of 1.0 mm and a length of 100 mm with a center of the test piece covered by a quartz tube and with a thermocouple attached. This was attached to an ohmic heating apparatus provided with a tensile device and was ohmically heated while cooling the two ends by a copper water cooling zone.
  • %Si, %Mn, %V, %Al, %Pb, and %S are the contents in steel (mass%).
  • the drawing value is 35% or more, the occurrence of cracks or flaws at the time of continuous casting can be sufficiently reduced. Accordingly, the R value found by the above formula (3) or formula (3') was limited to 35 or more. Note that, the upper limit of the R value is due to the amounts of the different elements, so is not particularly set.
  • C ensures the tensile strength and hardness of the part. To give good fractureability, 0.23% or more is required. On the other hand, if increasing the C, pearlite increases and the yield ratio deteriorates. Therefore, even if adjusting the alloy element to raise the tensile strength or hardness, the yield strength will not improve that much. Not only that, the fractureability and machineability will deteriorate, so the upper limit was limited to 0.35%. Further, C forms carbides with V and strengthens ferrite by precipitation strengthening. Preferably, the content is 0.28 to 0.32%.
  • Si is an element essential for promoting ferrite transformation and increasing the ferrite fraction. Further, Si strengthens ferrite by solution strengthening and lowers the ductility. To lower the ductility of the ferrite, 0.70% or more is necessary. However, if over 1.30%, the hot ductility deteriorates. From the viewpoint of ensuring hot ductility, 1.05% or less is preferable. More preferably, the content is 0.80 to 1.05%.
  • Mn is a solid-solution strengthening element and simultaneously an element promoting bainite transformation.
  • the upper limit is made 1.17%.
  • Mn is necessary for fixing the S in the steel as a sulfide and raising the hot ductility.
  • the lower limit is made 0.76%.
  • the content is 0.80 to 1.00%.
  • P is an element promoting ferrite transformation and suppressing bainite transformation.
  • 0.040% or more is necessary.
  • the upper limit is made 0.080%. From the viewpoint of ensuring the hot ductility, less than 0.065% is preferable. More preferably, the content is 0.045 to 0.062%.
  • the lower limit is made 0.040%. However, if adding this in a large amount, the anisotropy of the mechanical properties becomes greater, so the upper limit is made 0.118%.
  • the content is 0.060 to 0.110%.
  • Cr like Mn, is a solid-solution strengthening element and simultaneously is an element promoting bainite transformation. To ensure tensile strength and hardness, 0.05% or more is added. However, Cr has a higher effect of promoting bainite transformation than even Mn, so to suppress bainite, the content is limited to 0.20% or less. Preferably, the content is 0.08 to 0.16%.
  • V is an element forming carbonitrides to strengthen the ferrite by precipitation strengthening, improve the yield strength and tensile strength, and reduce the ductility. Further, V carbonitrides have the action of promoting ferrite transformation, so the low ductility fine ferrite increases. As a result, the breakage deformation is reduced and the peeling and other variations in fracture surfaces are also reduced.
  • V is limited to 0.27% or more. However, if over 0.45%, the effect becomes saturated and the cost also rises, so the upper limit is made 0.45%.
  • the content is 0.30 to 0.41%, more preferably 0.32 to 0.37%.
  • N is an element mainly forming V nitrides and V carbonitrides to suppress bainite transformation and promote ferrite transformation.
  • the lower limit is made 0.0050%. If added excessively, the hot ductility deteriorates and cracks or flaws easily form, so the upper limit is made 0.0145%. Preferably, the content is 0.0055 to 0.0135%.
  • the present invention has the above composition of ingredients as its basic ingredients, but may further optionally contain other elements. Below, the optional elements will be explained.
  • Ca, Zr, Te, and Ti are all elements refining sulfides.
  • the dispersion of fine sulfides in the present invention prevents the coarsening of the austenite structure right after hot forging and as a result promotes the ferrite transformation.
  • the coarse oxides and sulfides formed become causes of a drop in hot ductility and machineability, so the upper limits of Ca, Zr, and Te are made 0.0030% and the upper limit of Ti is made 0.050%.
  • Ti has the effect of refining sulfides and suppressing bainite transformation, but preferentially forms nitrides, so if added excessively, reduces the amount of production of V nitrides resulting in the undesirable phenomenon of the reduction in the amount of ferrite. For this reason, when adding Ti, 0.040% or less is more preferable.
  • Pb is added for improving the machineability.
  • Pb has the effect of reducing the hot ductility, so is limited to 0.050% or less.
  • 0.010% or more is required.
  • Al as shown by the above formula (3) and formula (3'), becomes a factor in the drop of the hot ductility, so is not positively added.
  • Al disperses as Al oxides in the steel and causes a drop in the machineability, so not adding Al is effective for ensuring machineability.
  • Al as an unavoidable impurity is made 0.010% or less.
  • Cu, Ni, and Mo are elements which can be freely included. If in fine amounts, they have no particular effect on the quality of the connecting rod, but each raises the quenchability and promotes bainite transformation.
  • the Cu and Ni contained as unavoidable impurities are both preferably 0.15% or less, while Mo is preferably 0.01% or less.
  • Nb similar to V, is an element having effects of precipitation strengthening and structure refinement. Part of the V can be replaced by Nb.
  • Nb carbonitrides compared with V carbonitrides, are higher in solution temperature and easily coarsen in the process of production of steel rod materials, so this is not aggressively added in the present invention.
  • the present invention was explained focusing on a connecting rod.
  • fracture split technology has not spread beyond connecting rods, but the present invention can also be applied, in the same way as to connecting rods, to other parts requiring fastening by accurate dimensional precision and parts which are repeatedly detached and reattached in maintenance work along with requiring assembly precision.
  • Invention steels (Invention Examples 1 to 24) and comparative steels (Comparative Examples 26 to 39 and conventional material) exhibiting the compositions of ingredients shown in Table 1 were melted in a 16 kg vacuum melting furnace to form ingots. These ingots were heated to 1493K, forged to steel rods of diameters of 55 mm, then allowed to cool. These were used as evaluation materials.
  • Table 1 No. C Si Mn P S Cr Al V N Ca Zr Te Ti Pb I n v . e x .
  • the test piece was made a rod shape of a diameter of 1.0 mm and a length of 100 mm, the center of the test piece was covered by a quartz tube, and a thermocouple was attached.
  • a steel rod material of a diameter of 55 mm was heated to 1503K, then forged vertically to the length direction of the steel rod to reduce the thickness to 20 mm, then was cooled by air blast cooling to room temperature. During the cooling, the average cooling rate from 1073K to 673K was 1.7K/s.
  • a tensile test piece and (2) a fracture test piece of a shape corresponding to the large end of a connecting rod were formed.
  • the shape and dimensions of the fracture test piece of the shape corresponding to the large end of a connecting rod are shown in FIG. 1 .
  • the test piece 1 is an 80 mmx80 mm, thickness 18 mm plate shape at the center of which a hole 2 of a diameter 50 mm is formed.
  • a hole 2 of a diameter 50 mm is formed on the inside surface of the diameter 50 mm hole.
  • 45° V-notches 3 of a depth of 1.0 mm and a front end rate of curvature of 0.5 mm were formed at two locations facing each other across 180° in a direction vertical to the length direction of the steel rod material before forging.
  • a through hole 4 of a diameter 8.0 mm was formed so that its center line became a position 8.0 mm from the side surface of the notched side.
  • the test apparatus is consisted of a split die and a falling weight tester.
  • the split die is consisted of a rectangular steel material on which is formed a cylinder split into two along the center line with one end fixed in place and the other end movable on a rail. At the mating surfaces of the two half cylinders, a shim hole is formed.
  • the test piece is fit in this split die, a shim is inserted, and the assembly is placed under a falling weight.
  • the falling weight has a weight of 200 kg and is designed to fall along a guide.
  • the shim When falling the falling weight, the shim is driven in and the test piece is broken into two by tension. Note that, to prevent the test piece from flying from the split die at the time of fracture, the test piece is fastened at its surroundings so as to be pressed against the split die.
  • test piece was fractured by a falling weight height of 100 mm, the fractured pieces of the test piece were aligned and bolted, and the changes in inside diameter in the fracture direction and direction vertical to the fracture direction were measured.
  • a ratio of less than 3% of bainite grains in the total number of proeutectoid ferrite grains and bainite grains was judged as no bainite structures and defined as ferrite-pearlite.
  • Table 2 shows the K value, F value, and R value and also the drawing value at the time of a hot tensile test, the presence of bainite in a material reproducing a forged connecting rod, the results of a tensile test at ordinary temperature, and the amount of deformation after a fracture test (total of amounts of change of inside diameter in XY directions).
  • Table 2 No. K value F value R value Bainite Ferrite frac. (%) Drawing (%) 0.2% YS (MPa) TS (MPa) X-dir. deform. ( ⁇ m) Y-dr. deform. ( ⁇ m) Deform. ( ⁇ m) I n v .
  • Nos. 1 to 24 are invention examples.
  • no bainite structure was formed, the ferrite fraction was 61% or more, and the drawing value at a hot tensile test was a good 37% or more.
  • the tensile strength at the ordinary temperature tensile test and the 0.2% yield strength were respectively 865 MPa or more and 693 MPa or more.
  • the 850 MPa or more tensile strength and the 650 MPa or more 0.2% yield strength aimed at by the present invention are realized.
  • the conventional steel C70S6 has a large C content, so the tensile strength (TS) is a high 995 MPa, but the 0.2% yield strength is a low 622 MPa.
  • Nos. 29, 30, 31, 38, and 39 are all low in R value and have drawing values in a hot tensile test of less than 35%, so production of an industrial steel material is difficult.
  • Nos. 33 to 37 are large in R value, but have Ca, Zr, and/ or Te added in large amounts, so the drawing value at the time of a hot tensile test is low.
  • the high strength fracture splitting use non-heat treated steel of the present invention is superior in hot ductility, becomes a stable ferrite-pearlite structure when hot forging, then air cooling or air blast cooling, and is superior in fracture splittability.
  • the steel part produced from the high strength fracture splitting use non-heat treated steel of the present invention is high in strength, small in amount of deformation at the time of fracture, and has a superior fracture splittability and further sufficiently provides the hot ductility required at the time of production. Accordingly, the present invention is high in industrial applicability.

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Claims (5)

  1. Hochfester, nicht wärmebehandelter Stahl für Fracture-Splitting-Verfahren, dadurch gekennzeichnet, dass er, in Massenprozent,
    C: 0,23 bis 0,35%,
    Si: 0,70 bis 1,30%,
    Mn: 0,76 bis 1,17%,
    P: 0,040 bis 0,080%,
    S: 0,040 bis 0,118%,
    Cr: 0,05 bis 0,20%,
    Al: 0,010% oder weniger,
    V: 0,27 bis 0,45%, und
    N: 0,0050 bis 0,0145%,
    und einen Rest von Fe und unvermeidbaren Verunreinigungen enthält, und
    einen K-Wert, der durch die folgende Formel (1) definiert ist, von 1,3 oder weniger, einen F-Wert, der durch die folgende Formel (2) definiert ist, von 3,0 oder weniger, und einen R-Wert, der durch die folgende Formel (3) definiert ist, von 35 oder mehr aufweist: K = - 0 , 56 × % C - 0 , 07 × % Si + 1 , 3 × % Mn + 0 , 80 × % Cr - 1 , 80 × % P + 0 , 19 % V - 5 , 6 × % N
    Figure imgb0017
     F = 4 , 3 × % C - 0 , 21 × % Si + 1 , 0 × % Mn + 1 , 4 × % Cr - 1 , 90 × % P + 1 , 8 % V - 6 , 6 × % N
    Figure imgb0018
     R = 46 , 7 - 7 , 4 × % Si + 37 , 7 × % Mn - 349 × % S - 12 , 0 × % V - 174 × % Al
    Figure imgb0019
    wobei %C, %Si, %Mn, %Cr, %P, %V, %N und %S Gehalte des Stahls (Massenprozent) sind, und %Al der Gehalt als Verunreinigung ist (Massenprozent).
  2. Hochfester, nicht wärmebehandelter Stahl für Fracture-Splitting-Verfahren gemäß Anspruch 1, dadurch gekennzeichnet, dass er darüber hinaus, in Massenprozent, eines oder mehrere von
    Ca: 0,0005 bis 0,0030%,
    Zr: 0,0005 bis 0,0030%,
    Te: 0,0005 bis 0,0030%, und
    Ti: 0,005 bis 0,050% enthält.
  3. Hochfester, nicht wärmebehandelter Stahl für Fracture-Splitting-Verfahren gemäß Anspruch 1 oder 2, dadurch gekennzeichnet, dass er darüber hinaus, in Massenprozent, Pb: 0,010 bis 0,050% enthält,
    und dadurch, dass er einen R-Wert, der anstatt durch obenstehende Formel (3) durch die folgende Formel (3') definiert ist, von 35 oder mehr aufweist. R = 46 , 7 - 7 , 4 × % Si + 37 , 7 × % Mn - 349 × % S - 12 , 0 × % V - 174 × % Al - 86 , 6 × % Pb
    Figure imgb0020
    wobei %Si, %Mn, %S, %V und %Pb Gehalte in dem Stahl (Massenprozent) sind und %Al der Gehalt als Verunreinigung (Massenprozent) ist.
  4. Ein hochfestes Stahlteil für Fracture-Splitting-Verfahren, hergestellt durch Warmschmieden und Kühlen eines hochfesten, nicht wärmebehandelten Stahls für Fracture-Splitting-Verfahren gemäß einem der Ansprüche 1 bis 3, wobei das Stahlteil dadurch gekennzeichnet ist, dass die gekühlte Stahlzusammensetzung eine Ferrit-Perlit-Struktur aufweist.
  5. Ein hochfestes Stahlteil für Fracture-Splitting-Verfahren gemäß Anspruch 4, dadurch gekennzeichnet, dass die Stahlzusammensetzung einen Volumenanteil an Ferrit von 60% oder mehr aufweist.
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