CN1498980A - Titanium-added, high strength steel - Google Patents
Titanium-added, high strength steel Download PDFInfo
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- CN1498980A CN1498980A CNA2003101017533A CN200310101753A CN1498980A CN 1498980 A CN1498980 A CN 1498980A CN A2003101017533 A CNA2003101017533 A CN A2003101017533A CN 200310101753 A CN200310101753 A CN 200310101753A CN 1498980 A CN1498980 A CN 1498980A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 153
- 239000010959 steel Substances 0.000 title claims abstract description 153
- 239000010936 titanium Substances 0.000 claims abstract description 77
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 42
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims abstract description 34
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 claims abstract description 32
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 17
- 239000012535 impurity Substances 0.000 claims description 18
- 229910052750 molybdenum Inorganic materials 0.000 claims description 12
- 229910052759 nickel Inorganic materials 0.000 claims description 12
- 238000002425 crystallisation Methods 0.000 claims description 9
- 230000008025 crystallization Effects 0.000 claims description 9
- 229910052796 boron Inorganic materials 0.000 claims description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 6
- 229910052804 chromium Inorganic materials 0.000 claims description 6
- 229910052760 oxygen Inorganic materials 0.000 claims description 5
- 239000011573 trace mineral Substances 0.000 claims description 4
- 235000013619 trace mineral Nutrition 0.000 claims description 4
- 229910052797 bismuth Inorganic materials 0.000 claims description 3
- 229910052742 iron Inorganic materials 0.000 claims description 3
- 229910052745 lead Inorganic materials 0.000 claims description 3
- 229910052711 selenium Inorganic materials 0.000 claims description 3
- 229910052717 sulfur Inorganic materials 0.000 claims description 3
- 229910052714 tellurium Inorganic materials 0.000 claims description 3
- 229910052782 aluminium Inorganic materials 0.000 claims description 2
- 229910052748 manganese Inorganic materials 0.000 claims description 2
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 abstract description 20
- 230000002411 adverse Effects 0.000 abstract description 2
- 238000010276 construction Methods 0.000 abstract 3
- 230000015572 biosynthetic process Effects 0.000 abstract 1
- -1 by weight Substances 0.000 abstract 1
- 239000000470 constituent Substances 0.000 abstract 1
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 230000000052 comparative effect Effects 0.000 description 12
- 238000004519 manufacturing process Methods 0.000 description 9
- 238000000034 method Methods 0.000 description 9
- 238000005520 cutting process Methods 0.000 description 8
- 238000012360 testing method Methods 0.000 description 8
- 238000005096 rolling process Methods 0.000 description 7
- 238000001816 cooling Methods 0.000 description 5
- 229910034327 TiC Inorganic materials 0.000 description 4
- 238000005266 casting Methods 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 102200082816 rs34868397 Human genes 0.000 description 4
- 238000007872 degassing Methods 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 238000005496 tempering Methods 0.000 description 3
- 238000005452 bending Methods 0.000 description 2
- 238000009749 continuous casting Methods 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 230000002401 inhibitory effect Effects 0.000 description 2
- 238000003754 machining Methods 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- 238000003303 reheating Methods 0.000 description 2
- 230000003068 static effect Effects 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910000954 Medium-carbon steel Inorganic materials 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 238000005255 carburizing Methods 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 125000004122 cyclic group Chemical group 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000000543 intermediate Substances 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000005457 optimization Methods 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 230000002829 reductive effect Effects 0.000 description 1
- 238000007619 statistical method Methods 0.000 description 1
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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
- C22C38/002—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
- C22C38/18—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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- Engineering & Computer Science (AREA)
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- Treatment Of Steel In Its Molten State (AREA)
Abstract
Disclosed is a titanium(Ti)-added steel wherein the formation of TiN or nitrogen-rich TiCN, which is found in a conventional titanium-added steel for machine construction and adversely affects the properties of the titanium-added steel for machine construction, has been suppressed, particularly a titanium-added, high strength steel wherein various properties can be stably exhibited and Ti(C)N has been regulated. This titanium-added, high strength steel is a steel for machine construction, which comprises, as steel constituents, by weight, titanium: not less than 500 ppm, the content of nitrogen (N) being N<100 ppm and has excellent fatigue limit as shown in 1.
Description
Technical field
The invention relates to the steel for mechanical structure for the parts of the various industrial machineries such as trolley part and device, particularly about take steel for mechanical structure as high-strength steel basic, that further added wherein the interpolation titanium of titanium.
Background technology
In the past, in the parts of the various industrial machines such as trolley part and device, conventionally use SC steel, SMn steel, SCr steel, SCM steel, SNC steel, SNCM steel and the SUJ steel of regulation in Japanese Industrial Standards (JIS), in these steel, further add the steel of B, and in these steel, further added the micro-steel for mechanical structure such as steel.
In addition, people also know the steel that has further added 500ppm (0.0500 quality %) or above titanium in these steel for mechanical structure, for example, referring to Unexamined Patent 8-283910, Unexamined Patent 10-130720, Unexamined Patent 10-251806, Unexamined Patent 11-293403 and Unexamined Patent 11-293392.In these documents, disclose, by add 500ppm or above titanium in steel for mechanical structure, can improve the characteristics such as various performances such as static strength, fatigue strength and grain fineness number of steel.
Summary of the invention
Recently, the present inventors find, in having added the steel for mechanical structure of titanium, by controlling TiN that in nitrogen content or steel, crystallization goes out and/or the overall dimension of TiCN
can obtain the high-strength steel of the interpolation titanium of the various excellent performances such as fatigue strength.In the high-strength steel of the interpolation titanium obtaining like this, the generation of the inclusiones such as TiCN of TiN or rich N is suppressed.
Therefore, the object of the invention is, the steel for mechanical structure of the interpolation titanium of the various excellent performances such as fatigue strength is provided.
That is, the high-strength steel of the interpolation titanium of the first embodiment of the present invention is by containing Ti:0.0500 quality % or above and N: the steel for mechanical structure of less than 0.0100 quality % forms.
The high-strength steel of the interpolation titanium of the second embodiment of the present invention, is by containing Ti:0.0500 quality % or above steel for mechanical structure forms, with extreme statistics prediction, at 30000mm
2the TiN that in steel in detected area, crystallization goes out and/or the overall dimension of TiCN
80 μ m or following.
The high-strength steel of the interpolation titanium of the 3rd embodiment of the present invention is by containing Ti:0.0500 quality % or above and N: the steel for mechanical structure of less than 0.0100 quality % forms, with extreme statistics prediction, at 30000mm
2the TiN that in steel in detected area, crystallization goes out and/or the overall dimension of TiCN
80 μ m or following.
Accompanying drawing explanation
Fig. 1 means in embodiment 1 figure that manufacture, the steel of first embodiment of the invention and the nitrogen content of comparative steel (quality %) thereof and the relation of safe range of stress (MPa).In figure, each mark is other a pair of numeral, and left-hand digit represents heat (batch) number No., the specimen coding in this heat (batch) number of the numeral on the right No..
Fig. 2 means in embodiment 2 overall dimension that manufacture, the of the present invention second and the 3rd steel of embodiment and the TiN of comparative steel thereof
figure with the relation of the safe range of stress (MPa) of rotating bending test.
Fig. 3 means in embodiment 2 overall dimension that manufacture, the of the present invention second and the 3rd steel of embodiment and the TiN of comparative steel thereof
figure with the relation of the TiN probability (%) of fracture origin.
Embodiment
Definition
In the present invention,
with the square root of the area of extreme statistics prediction, the maximum non-metallic inclusion that exists in the area of detection of regulation, be TiN that in steel, crystallization goes out and/or the overall dimension of TiCN in the present invention.
" extreme statistics " is a kind of known method, that is,, by cutting a plurality of test pieces on a steel billet, measure the maximum diameter of the inclusion in each test piece, suppose that the existence of the inclusion with maximum diameter, by statistical distribution, infers the maximum diameter of the inclusion existing in prescribed volume.The method is for example respected suitable in village: " metal fatigue " tiny flaw and the impact being situated between at thing " ", (1993), support in virtuous hall and have detailed explanation.General inclusion assessment method is mainly the quantity of evaluating inclusion, and on the other hand, extreme statistics is to adopt statistical method to infer " size (extreme value) of the maximum inclusion existing " in a certain size region (dangerous volume).This method is used the " square root of the shadow area while inclusion being projected in the plane of specific direction
as " index of inclusion size ".Then, according to detected maximum inclusion in several detected areas
distribution, adopt statistical treatment to infer " the maximum inclusion in dangerous volume
?
Add the high-strength steel of titanium
The high-strength steel of interpolation titanium of the present invention, is to take steel for mechanical structure as basis, further adds titanium and the TiN that in restriction nitrogen content or steel, crystallization goes out and/or the overall dimension of TiCN in this steel for mechanical structure
steel.
In steel of the present invention, the content of titanium be 0.0500 quality % or more than, preferably 0.080-0.200 quality %, more preferably 0.10-0.18 quality %.By add titanium in above-mentioned scope, can improve the various performances of steel for mechanical structure, characteristics such as static strength, fatigue strength, grain fineness number.
According to a preferred embodiment of the invention, the nitrogen content in steel is less than 0.0100 quality %, preferably less than 0.0080 quality %, more preferably 0.0020-0.0070 quality %.Nitrogen content in above-mentioned scope time, can be brought into play the performance of the steel that adds titanium effectively.That is, generally, in adding the steel of titanium, by adding titanium, make to separate out the TiC of 100nm or following size or the TiCN of rich C in steel, can obtain excellent performance.But, when titanium reacts with nitrogen and carbon, when crystallization goes out the non-metallic inclusion consisting of the TiCN of TiN or rich nitrogen (below the two being referred to as to " TiN "), can think that this inclusion will produce adverse influence to the performance of steel.Therefore, by the nitrogen content in steel is limited in above-mentioned scope, can suppress the crystallization of TiN, make titanium form the form of 100nm or the precipitation type TiC of following size or the TiCN of rich C.Result has been got rid of above-mentioned disadvantageous effect, can effectively bring into play the performance of the steel that adds titanium.
According to a preferred embodiment of the invention, by the overall dimension of TiN
be limited to 80 μ m or following, preferably 60 μ m or following, more preferably 0-50 μ m.
in the time of in above-mentioned scope, can realize high intensity.That is, the TiN of crystal type, by with steel in the size of the oxide-based inclusion that contains keep in balance, likely become the starting point of repeated stress failure.Specifically, according to the present inventors' opinion, when the overall dimension of TiN surpasses 80 μ m, the possibility that its size is larger than oxide-based inclusion increases, thereby TiN becomes the origin of repeated stress failure.In this case, if be in, cause that take inclusion is the working conditions of the repeated stress failure of origin, its intensity will be lower than the steel that does not add Ti.Therefore, the overall dimension of TiN is limited to 80 μ m or following, makes it the size that reaches with oxide-based inclusion identical or less, the situation that above-mentioned intensity is low has not just existed.
According to a preferred embodiment of the invention, the high-strength steel that adds titanium be the steel for mechanical structure being selected from SC steel (JISG4051 (1979)), SMn steel (JISG 4106 (1979)), SCr steel (JISG 4104 (1979)), SCM steel (JISG 4105 (1979)), SNC steel (JISG 4102 (1979)), SNCM steel (JISG4103 (1979)) and SUJ steel (JISG 4805 (1999)) be basic steel.According to the embodiment of present invention further optimization, take above-mentioned steel for mechanical structure as basic steel, be that to contain Ti and N, trace element as required, surplus be iron and the inevitable steel of impurity, and meet the condition of above-mentioned Ti, N and TiC and TiCN.
" trace element " described in the present invention, refers to approximately 0.5% or steel is produced during following content the element of useful effect.In addition, described " as required " refer to, according to the needs of purposes, can contain arbitrarily, also can not contain completely.
Representational example as trace element can be enumerated following example.Al is the element often using as deoxidant element, and maximum can contain 0.05%.B is the element that improves hardening capacity, and maximum can contain 0.0050 quality %.Pb, Bi, Te and Se are the elements that improves cutting ability, and maximum can contain 0.3%.Equally, Ca maximum can contain 0.010%, S maximum and can contain 0.3%.In addition, in order to improve cutting ability, S content can surpass 0.05%, preferably 0.1% or more than, paying attention to physical strength and be better than the occasion of cutting ability, its content should be 0.05% or following.
According to a preferred embodiment of the invention, the high-strength steel of above-mentioned interpolation titanium contains (quality %) C:0.10～1.20%, Si:0.05～2.0%, Mn:0.05～2.0%, Ti:0.0500～0.25%, N:0.0020～0.0100%, as required, P:0～0.050%, O:0～0.0030%, Ni:0～3.00%, Cr:0～3.00%, Mo:0～3.00%, Al:0～0.05%, B:0～0.0050%, Pb:0～0.3%, Bi:0～0.3%, Te:0～0.3%, Se:0～0.3%, Ca:0～0.010%, S:0～0.3%, surplus is iron and inevitable impurity.
Manufacture method
The Production Example of the high-strength steel of interpolation titanium of the present invention is as carried out according to following.First, use the steel of electrosmelting predetermined component.Then, use steel teeming ladle refined molten steel, regulate the alloy amount of molten steel, meanwhile molten steel is added the Al of 0.015-0.023 quality %, reduce oxygen amount (Al deoxidation), then carry out RH degassing processing.In the latter stage of degassing processing, add Ti, the amount of 2.0 times of molten steel amount is refluxed, be smelted into 150 tons of molten steel with the titanium content in 0.05-0.20 quality % (500-2000ppm) scope.
At 1570 ℃, these molten steel are transferred to tundish from steel teeming ladle, use continuous casting loading amount, be cast as the large section casting blank with 380mm * 450mm section.Now, with the casting speed traction strand of 0.45 meter per second, below casting relief outlet, 36 meters of cut into strand with gas cutting machine.Resulting strand is transported to breaking down cogging operation.Molten steel from by casting during relief outlet the time during to gas cutting be equivalent to 80 minutes.
By the strand cutting obtaining like this, this cutting surfaces is used HCL aqueous corrosion after polishing, observes metallographic structure, according to the interval of its dendritic arm, can infer speed of cooling.According to the inventor's mensuration, even near the strand center of final set, speed of cooling also reaches 1.1 ℃/min.
Subsequently, gained strand is paid to breaking down cogging operation.In this breaking down cogging operation, by strand be heated to 1180 ℃ or more than, then hot rolling obtains the steel of φ 150.By resulting Steel Rolling, make intermediates.This rolling is to carry out in 1180 ℃ or above temperature range from start to finish, is cooled fast to 1100 ℃ or following after rolling, and the particle diameter of the precipitates such as TiCN of TiC or rich C can not grown up.
In addition, the less occasion of size at rolling time after shorter and rolling, cooling after rolling also can be undertaken by air cooling, in other occasion in addition, also can utilize water-cooled or the method such as air-cooled cooling fast, inhibiting grain growth.Particularly under rolling state to forming the occasion not reheating before the finished product, adopt such temperature-controlled process just enough.On the other hand, in the time of being processed into parts, the occasion reheating in order to carry out heat forged after rolling, must carry out the temperature for inhibiting grain growth same with above-mentioned hot rolling and control.
Embodiment
According to manufacture method recited above, for the steel of the interpolation Ti shown in each heat (batch) number No. manufacture below.
Heat (batch) number No.1: take the steel of SCr420 as basic interpolation Ti
Heat (batch) number No.2: take the steel of SCM420 as basic interpolation Ti
Heat (batch) number No.3: take the steel of SNCM420 as basic interpolation Ti
Heat (batch) number No.4: take the steel of SNC415 as basic interpolation Ti
Heat (batch) number No.5: take the steel of S45C as basic interpolation Ti
Heat (batch) number No.6: take the steel of SMn443 as basic interpolation Ti
Heat (batch) number No.7: take the steel of SUJ2 as basic interpolation Ti
Heat (batch) number No.8: the steel that has added B and Ti in SCr420
Now, for each heat (batch) number No., by changing degasification time, the steel of melting different N content.
Shown in table 1, supply the chemical composition of examination material.Shown in this table, as basic steel and the chemical composition thereof of each heat (batch) number No., be described as follows.
Heat (batch) number No.1 is SCr420, and wherein inevitably impurity is Ni and Mo.Heat (batch) number No.2 is SCM420, and wherein inevitably impurity is Ni.Heat (batch) number No.3 is SNCM420.Heat (batch) number No.4 is SNC415, and wherein inevitably impurity is Mo.Heat (batch) number No.5 is S45, and wherein inevitably impurity is Ni, Cr and Mo.Heat (batch) number No.6 is SMn443, and wherein inevitably impurity is Ni, Cr and Mo.Heat (batch) number No.7 is SUJ2, and wherein inevitably impurity is Ni and Mo.Heat (batch) number No.8 is the steel that has added B in SUJ2, and wherein inevitably impurity is Ni and Mo.
Table 1
Unit: quality %, wherein the unit of Ti, O, N and B is ppm
| Heat (batch) number No. | ??C | ?Si | ??Mn | ??P | ?S | ??Ni | ??Cr | ?Mo | ??Ti | ??O | ??N | ??B | Remarks | |
| ????1 | 1 | ??0.20 | ??0.25 | ??0.80 | ??0.014 | ??0.018 | ??0.06 | ??1.13 | ??0.02 | ?1459 | ??9 | ??90 | ??- | The first embodiment |
| 2 | ??0.21 | ??0.25 | ??0.81 | ??0.015 | ??0.018 | ??0.06 | ??1.13 | ??0.02 | ?980 | ??8 | ??72 | ??- | The first embodiment | |
| 3 | ??0.20 | ??0.25 | ??0.80 | ??0.014 | ??0.017 | ??0.05 | ??1.14 | ??0.02 | ?580 | ??9 | ??66 | ??- | The first embodiment | |
| 4 | ??0.21 | ??0.26 | ??0.80 | ??0.013 | ??0.018 | ??0.06 | ??1.13 | ??0.02 | ?1525 | ??9 | ??102 | ??- | Comparative steel | |
| 5 | ??0.21 | ??0.25 | ??0.80 | ??0.014 | ??0.018 | ??0.06 | ??1.13 | ??0.02 | ?1501 | ??10 | ??110 | ??- | Comparative steel | |
| 6 | ??0.20 | ??0.26 | ??0.79 | ??0.013 | ??0.018 | ??0.05 | ??1.14 | ??0.02 | ?1133 | ??10 | ??81 | ??- | The first embodiment | |
| 7 | ??0.20 | ??0.26 | ??0.79 | ??0.014 | ??0.017 | ??0.06 | ??1.13 | ??0.02 | ?1942 | ??10 | ??77 | ??- | The first embodiment | |
| ????2 | 1 | ??0.20 | ??0.25 | ??0.82 | ??0.013 | ??0.017 | ??0.07 | ??1.11 | ??0.15 | ?1378 | ??8 | ??61 | ??- | The first embodiment |
| 2 | ??0.21 | ??0.25 | ??0.79 | ??0.012 | ??0.019 | ??0.07 | ??1.15 | ??0.15 | ?1482 | ??9 | ??115 | ??- | Comparative steel | |
| ????3 | 1 | ??0.21 | ??0.23 | ??0.55 | ??0.015 | ??0.016 | ??1.61 | ??0.51 | ??0.15 | ?1466 | ??9 | ??65 | ??- | The first embodiment |
| 2 | ??0.20 | ??0.25 | ??0.55 | ??0.015 | ??0.018 | ??1.61 | ??0.52 | ??0.15 | ?1527 | ?10 | ?109 | ??- | Comparative steel | |
| ????4 | 1 | ??0.17 | ??0.23 | ??0.51 | ??0.015 | ??0.017 | ??1.97 | ??0.40 | ??0.01 | ?1472 | ?10 | ?67 | ??- | The first embodiment |
| 2 | ??0.17 | ??0.25 | ??0.51 | ??0.017 | ??0.018 | ??1.99 | ??0.40 | ??0.01 | ?1390 | ??9 | ?115 | ??- | Comparative steel | |
| ????5 | 1 | ??0.45 | ??0.27 | ??0.82 | ??0.016 | ??0.018 | ??0.08 | ??0.12 | ??0.01 | ?1499 | ??8 | ?66 | ??- | The first embodiment |
| 2 | ??0.45 | ??0.26 | ??0.82 | ??0.014 | ??0.018 | ??0.08 | ??0.12 | ??0.01 | ?1523 | ??8 | ?107 | ??- | Comparative steel | |
| ????6 | 1 | ??0.42 | ??0.23 | ??1.55 | ??0.013 | ??0.015 | ??0.09 | ??0.13 | ??0.01 | ?1377 | ??9 | ?71 | ??- | The first embodiment |
| 2 | ??0.41 | ??0.24 | ??1.53 | ??0.012 | ??0.016 | ??0.09 | ??0.14 | ??0.01 | ?1456 | ??9 | ?109 | ??- | Comparative steel | |
| ????7 | 1 | ??1.00 | ??0.24 | ??0.44 | ??0.010 | ??0.008 | ??0.10 | ??1.42 | ??0.01 | ?1271 | ??7 | ?61 | ??- | The first embodiment |
| 2 | ??1.00 | ??0.23 | ??0.45 | ??0.010 | ??0.008 | ??0.10 | ??1.41 | ??0.01 | ?1362 | ??7 | ?111 | ??- | Comparative steel | |
| ????8 | 1 | ??0.20 | ??0.25 | ??0.75 | ??0.014 | ??0.013 | ??0.05 | ??1.14 | ??0.01 | ?1451 | ??9 | ?66 | ??13 | The first embodiment |
| 2 | ??0.21 | ??0.26 | ??0.76 | ??0.013 | ??0.015 | ??0.06 | ??1.13 | ??0.02 | ?1508 | ??9 | ?120 | ??16 | Comparative steel |
By resulting strand heating, to extend and be forged into φ 20mm, machining after normalizing, obtains rotoflector sample.The steel of the interpolation Ti of SUJ2 quenches and tempering, and the steel of the interpolation Ti of S45C and SMn443 carries out high-frequency quenching and tempering, and the steel of other interpolation Ti carries out carburizing and quenching and tempering, makes its surface hardening.By the test position surface finishing polish of each sample, then use little wild formula rotating bending fatigue machine to carry out the determination test of safe range of stress.
The N content (ppm) obtaining through safe range of stress test shown in table 1 and the relation of rotoflector fatigue strength (MPa).As shown in the figure, when N content surpasses 80ppm, safe range of stress (10
7inferior cyclic fatigue intensity) start to reduce, its content is at 100ppm or when above, and fatigue strength greatly reduces.Can think this be due to, along with the increase of N content, due to the harmful TiN of fatigue strength is increased.
Embodiment 2
According to manufacture method recited above, for the steel of the interpolation Ti shown in each heat (batch) number No. manufacture below.
Heat (batch) number A: take the steel of SCr420 as basic interpolation Ti
Heat (batch) number B: take the steel of SCM420 as basic interpolation Ti
Heat (batch) number C: take the steel of SNCM420 as basic interpolation Ti
Heat (batch) number D: take the steel of SNC415 as basic interpolation Ti
Heat (batch) number E: take the steel of S45C as basic interpolation Ti
Heat (batch) number F: take the steel of SMn443 as basic interpolation Ti
Heat (batch) number G: take the steel of SUJ2 as basic interpolation Ti
Heat (batch) number H: the steel that has added B and Ti in SUJ2
Now, for each heat (batch) number, the setting rate while controlling continuous casting, obtains the steel of the interpolation Ti that the size of TiN is different, by this steel, makes sample.
Shown in table 2, this adds the composition of the steel of Ti.Shown in this table, as basic steel and the chemical composition thereof of each heat (batch) number, be described as follows.
Heat (batch) number A is SCr420, and wherein inevitably impurity is Ni and Mo.Heat (batch) number B is SCM420, and wherein inevitably impurity is Ni.Heat (batch) number C is SNCM420.Heat (batch) number D is SNC415, and wherein inevitably impurity is Mo.Heat (batch) number E is S45C, and wherein inevitably impurity is Ni, Cr and Mo.Heat (batch) number F is SMn443, and wherein inevitably impurity is Ni, Cr and Mo.Heat (batch) number G is SUJ2, and wherein inevitably impurity is Ni and Mo.Heat (batch) number H is the steel that adds B in SUJ2, and wherein inevitably impurity is Ni and Mo.
Table 2
Unit: quality %, wherein the unit of Ti, O, N and B is ppm
| Heat (batch) number NO. | ????C | ????Si | ??Mn | ????P | ????S | ????Ni | ????Cr | ????Mo | ????Ti | ??O | ??N | ?B | |
| ??A | ??1 | ?0.20 | ??0.26 | ??0.80 | ??0.015 | ??0.018 | ??0.06 | ??1.13 | ??0.02 | ??1556 | ??10 | ??64 | ?- |
| ??2 | ?0.20 | ??0.26 | ??0.79 | ??0.014 | ??0.018 | ??0.06 | ??1.13 | ??0.02 | ??920 | ??9 | ??87 | ?- | |
| ??3 | ?0.20 | ??0.25 | ??0.80 | ??0.015 | ??0.017 | ??0.06 | ??1.13 | ??0.02 | ??1446 | ??12 | ??71 | ?- | |
| ??4 | ?0.21 | ??0.25 | ??0.79 | ??0.15 | ??0.018 | ??0.06 | ??1.14 | ??0.02 | ??1440 | ??11 | ??102 | ?- | |
| ??5 | ?0.20 | ??0.25 | ??0.79 | ??0.014 | ??0.017 | ??0.06 | ??1.12 | ??0.03 | ??1901 | ??10 | ??128 | ?- | |
| ??6 | ?0.20 | ??0.25 | ??0.80 | ??0.014 | ??0.018 | ??0.06 | ??1.13 | ??0.02 | ??568 | ??10 | ??70 | ?- | |
| ??7 | ?0.20 | ??0.25 | ??0.81 | ??0.014 | ??0.017 | ??0.06 | ??1.13 | ??0.02 | ??1295 | ??11 | ??62 | ?- | |
| ??8 | ?0.21 | ??0.25 | ??0.79 | ??0.014 | ??0.017 | ??0.07 | ??1.12 | ??0.02 | ??1498 | ??10 | ??112 | ?- | |
| ??9 | ?0.21 | ??0.25 | ??0.80 | ??0.015 | ??0.017 | ??0.06 | ??1.13 | ??0.02 | ??1522 | ??12 | ??74 | ?- | |
| ??10 | ?0.20 | ??0.25 | ??0.79 | ??0.015 | ??0.018 | ??0.06 | ??1.13 | ??0.02 | ??1484 | ??10 | ??63 | ?- | |
| ??11 | ?0.20 | ??0.25 | ??0.80 | ??0.015 | ??0.017 | ??0.05 | ??1.13 | ??0.02 | ??1154 | ??11 | ??84 | ?- | |
| ??12 | ?0.20 | ??0.25 | ??0.80 | ??0.015 | ??0.018 | ??0.06 | ??1.13 | ??0.02 | ??1446 | ??10 | ??114 | ?- | |
| ??B | ??1 | ?0.20 | ??0.25 | ??0.81 | ??0.013 | ??0.017 | ??0.07 | ??1.12 | ??0.16 | ??1654 | ??8 | ??77 | ?- |
| ??2 | ?0.21 | ??0.26 | ??0.79 | ??0.011 | ??0.016 | ??0.09 | ??1.16 | ??0.15 | ??1427 | ??8 | ??111 | ?- | |
| ??C | ??1 | ?0.22 | ??0.25 | ??0.54 | ??0.017 | ??0.016 | ??1.62 | ??0.52 | ??0.15 | ??1167 | ??9 | ??108 | ?- |
| ??2 | ?0.20 | ??0.25 | ??0.56 | ??0.015 | ??0.018 | ??1.63 | ??0.51 | ??0.15 | ??1361 | ??10 | ??99 | ?- | |
| ??D | ??1 | ?0.17 | ??0.25 | ??0.57 | ??0.016 | ??0.017 | ??1.99 | ??0.42 | ??0.01 | ??1098 | ??11 | ??88 | ?- |
| ??2 | ?0.17 | ??0.25 | ??0.55 | ??0.016 | ??0.018 | ??1.97 | ??0.44 | ??0.01 | ??1762 | ??8 | ??62 | ?- | |
| ??E | ??1 | ?0.45 | ??0.27 | ??0.85 | ??0.015 | ??0.016 | ??0.06 | ??0.11 | ??0.01 | ??1468 | ??8 | ??70 | ?- |
| ??2 | ?0.45 | ??0.27 | ??0.81 | ??0.014 | ??0.017 | ??0.08 | ??0.12 | ??0.01 | ??1490 | ??8 | ??120 | ?- | |
| ??F | ??1 | ?0.41 | ??0.23 | ??1.58 | ??0.011 | ??0.017 | ??0.09 | ??0.16 | ??0.01 | ??1478 | ??9 | ??65 | ?- |
| ??2 | ?0.42 | ??0.25 | ??1.55 | ??0.016 | ??0.018 | ??0.10 | ??0.15 | ??0.01 | ??1522 | ??9 | ??101 | ?- | |
| ??G | ??1 | ?1.00 | ??0.25 | ??0.40 | ??0.010 | ??0.008 | ??0.10 | ??1.40 | ??0.01 | ??1548 | ??8 | ??105 | ?- |
| ??2 | ?1.00 | ??0.23 | ??0.44 | ??0.011 | ??0.007 | ??0.10 | ??1.42 | ??0.01 | ??1422 | ??6 | ??67 | ?- | |
| ??H | ??1 | ?0.20 | ??0.26 | ??0.77 | ??0.017 | ??0.011 | ??0.05 | ??1.17 | ??0.01 | ??1444 | ??9 | ??67 | ?15 |
| ??2 | ?0.21 | ??0.27 | ??0.77 | ??0.017 | ??0.015 | ??0.06 | ??1.16 | ??0.02 | ??1633 | ??9 | ??108 | ?18 |
By the steel heating of the steel of resulting interpolation Ti, to extend and be forged into φ 20mm, machining after normalizing, obtains rotoflector sample, is rotated similarly to Example 1 pliability test.
Shown in Fig. 2, through safe range of stress test, obtain,
relation with rotoflector fatigue strength (MPa).In Fig. 2, " zero " represents medium carbon steel.As shown in the figure,
while surpassing 60 μ m, safe range of stress reduces, and while surpassing 80 μ m, safe range of stress further reduces.
For all samples of steel shown in table 2, investigation forms the non-metallic inclusion of fracture origin, determines
the probability (%) that safe range of stress (MPa) and the TiN of take are fracture origin.Result is as shown in table 3.In addition, measurement result shown in Fig. 3, wherein, the longitudinal axis represents the TiN probability of fracture origin, transverse axis represents TiN's
as shown in table 3, when TiN's
during increase, the probability that TiN becomes fracture origin raises, and while surpassing 80 μ m, is nearly all to take TiN to occur disrumpent feelings as fracture origin.That is,
at 60 μ m when following, because TiN is less than oxide-based inclusion, thereby oxide-based inclusion becomes fracture origin, and Ti is that inclusion is for not impact of fatigue strength.Otherwise,
at 80 μ m or when above, TiN is larger than oxide-based inclusion, so repeated stress failure major part is to take TiN as fracture origin, and fatigue strength is reduced.By this result, can find out the impact of the size of TiN on fatigue strength.
Table 3
Claims (5)
1. a high-strength steel that adds titanium, is characterized in that, is by containing Ti:0.0500 quality % or above and N: the steel for mechanical structure of less than 0.0100 quality % forms.
2. a high-strength steel that adds titanium, is characterized in that, is by containing Ti:0.0500 quality % or above steel for mechanical structure forms, with extreme statistics prediction, at 30000mm
2the TiN that in steel in detected area, crystallization goes out and/or the overall dimension of TiCN
80 μ m or following.
3. a high-strength steel that adds titanium, is characterized in that, is by containing Ti:0.0500 quality % or above and N: the steel for mechanical structure of less than 0.0100 quality % forms, with extreme statistics prediction, at 30000mm
2the TiN that in steel in detected area, crystallization goes out and/or the overall dimension of TiCN
80 μ m or following.
4. the high-strength steel of the interpolation titanium described in any one in claim 1-3, it is characterized in that, to be selected from steel in SC steel (JISG 4051 (1979)), SMn steel (JISG 4106 (1979)), SCr steel (JISG 4104 (1979)), SCM steel (JISG 4105 (1979)), SNC steel (JISG 4102 (1979)), SNCM steel (JISG 4103 (1979)) and SUJ steel (JISG 4805 (1999)) for basis, make wherein to contain Ti and N, contain as required trace element and contain the steel that inevitable impurity element forms.
5. the high-strength steel of the interpolation titanium described in any one in claim 1-3, it is characterized in that, in quality %, contain C:0.10～1.20%, Si:0.05～2.0%, Mn:0.05～2.0%, Ti:0.0500～0.25%, N:0.0020～0.0100%, also contain as required P:0～0.050%, O:0～0.0030%, Ni:0～3.00%, Cr:0～3.00%, Mo:0～3.00%, Al:0～0.05%, B:0～0.0050%, Pb:0～0.3%, Bi:0～0.3%, Te:0～0.3%, Se:0～0.3%, Ca:0～0.010%, S:0～0.3%, surplus is iron and inevitable impurity.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2002311178A JP2004143550A (en) | 2002-10-25 | 2002-10-25 | Ti-ADDED HIGH STRENGTH STEEL |
| JP311178/2002 | 2002-10-25 |
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| CN1293221C CN1293221C (en) | 2007-01-03 |
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| CN102383052A (en) * | 2011-10-13 | 2012-03-21 | 浪莎针织有限公司 | High wear resistance steel for knitting needle and manufacture method thereof |
| CN103627979A (en) * | 2013-11-12 | 2014-03-12 | 铜陵市肆得科技有限责任公司 | Large-sized pump bearing steel material and preparation method thereof |
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| JP2015183706A (en) * | 2014-03-20 | 2015-10-22 | Ntn株式会社 | Bearing ring and rolling bearing having bearing ring |
| CN110773219B (en) * | 2019-10-30 | 2022-01-11 | 中国海洋大学 | photo-Fenton desulfurization and denitrification catalyst and preparation method thereof |
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| US4472208A (en) * | 1982-06-28 | 1984-09-18 | Sumitomo Metal Industries, Ltd. | Hot-rolled high tensile titanium steel plates and production thereof |
| JP3432950B2 (en) * | 1995-04-17 | 2003-08-04 | 新日本製鐵株式会社 | Steel material for induction hardened shaft parts that has both cold workability and torsional fatigue strength characteristics |
| JPH10130720A (en) * | 1996-10-23 | 1998-05-19 | Sanyo Special Steel Co Ltd | Production of case hardening boron steel excellent in grain size characteristic |
| JPH10251806A (en) * | 1997-03-14 | 1998-09-22 | Sanyo Special Steel Co Ltd | Steel excellent in rolling fatigue life |
| JP4505064B2 (en) * | 1998-02-16 | 2010-07-14 | 三井化学株式会社 | Ground consolidation improver |
| JP3426496B2 (en) * | 1998-04-09 | 2003-07-14 | 山陽特殊製鋼株式会社 | High strength long life carburizing steel excellent in delayed fracture resistance and method of manufacturing the same |
| DE19928775C2 (en) * | 1998-06-29 | 2001-10-31 | Nsk Ltd | Induction hardened roller bearing device |
| JP2001020030A (en) * | 1999-07-02 | 2001-01-23 | Kobe Steel Ltd | High strength hot rolled steel plate excellent in stretch-flange formability |
| JP3565428B2 (en) * | 2000-10-02 | 2004-09-15 | 株式会社住友金属小倉 | Steel for machine structure |
| JP3753101B2 (en) * | 2002-07-03 | 2006-03-08 | 住友金属工業株式会社 | High strength and high rigidity steel and manufacturing method thereof |
| JP4168721B2 (en) * | 2002-10-10 | 2008-10-22 | 住友金属工業株式会社 | High-strength steel and manufacturing method thereof |
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| CN102383052A (en) * | 2011-10-13 | 2012-03-21 | 浪莎针织有限公司 | High wear resistance steel for knitting needle and manufacture method thereof |
| CN103627979A (en) * | 2013-11-12 | 2014-03-12 | 铜陵市肆得科技有限责任公司 | Large-sized pump bearing steel material and preparation method thereof |
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