CN101492787B - Medium-high-carbon microalloy non-hardened and tempered steel and controlled forging and cooling process - Google Patents
Medium-high-carbon microalloy non-hardened and tempered steel and controlled forging and cooling process Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 79
- 239000010959 steel Substances 0.000 title claims abstract description 79
- 229910052799 carbon Inorganic materials 0.000 title claims abstract description 74
- 238000005242 forging Methods 0.000 title claims abstract description 70
- 238000000034 method Methods 0.000 title claims abstract description 40
- 230000008569 process Effects 0.000 title claims abstract description 29
- 238000001816 cooling Methods 0.000 title abstract description 26
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 73
- 238000010438 heat treatment Methods 0.000 claims abstract description 32
- 239000000203 mixture Substances 0.000 claims abstract description 16
- 238000005520 cutting process Methods 0.000 claims abstract description 7
- 238000003672 processing method Methods 0.000 claims description 33
- 229910052719 titanium Inorganic materials 0.000 claims description 12
- 229910052720 vanadium Inorganic materials 0.000 claims description 12
- 230000000903 blocking effect Effects 0.000 claims description 6
- 238000004080 punching Methods 0.000 claims description 6
- 238000010080 roll forging Methods 0.000 claims description 6
- 239000004615 ingredient Substances 0.000 claims description 4
- 239000000956 alloy Substances 0.000 abstract 3
- 229910045601 alloy Inorganic materials 0.000 abstract 3
- 238000005266 casting Methods 0.000 abstract 1
- 235000013619 trace mineral Nutrition 0.000 abstract 1
- 239000011573 trace mineral Substances 0.000 abstract 1
- 238000009966 trimming Methods 0.000 abstract 1
- 238000004519 manufacturing process Methods 0.000 description 15
- 239000010955 niobium Substances 0.000 description 13
- 239000010936 titanium Substances 0.000 description 13
- 229910000859 α-Fe Inorganic materials 0.000 description 12
- 229910001566 austenite Inorganic materials 0.000 description 10
- 235000019362 perlite Nutrition 0.000 description 10
- 239000010451 perlite Substances 0.000 description 10
- 239000013078 crystal Substances 0.000 description 8
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 6
- 238000010586 diagram Methods 0.000 description 6
- 238000005516 engineering process Methods 0.000 description 6
- 239000011572 manganese Substances 0.000 description 6
- 239000000463 material Substances 0.000 description 6
- 229910052758 niobium Inorganic materials 0.000 description 6
- 239000002994 raw material Substances 0.000 description 6
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 5
- 238000013461 design Methods 0.000 description 5
- 238000011161 development Methods 0.000 description 5
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 5
- 238000012545 processing Methods 0.000 description 5
- 238000010791 quenching Methods 0.000 description 5
- 230000009467 reduction Effects 0.000 description 5
- GPPXJZIENCGNKB-UHFFFAOYSA-N vanadium Chemical compound [V]#[V] GPPXJZIENCGNKB-UHFFFAOYSA-N 0.000 description 5
- 238000009826 distribution Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 230000000171 quenching effect Effects 0.000 description 4
- 238000005496 tempering Methods 0.000 description 4
- 238000007669 thermal treatment Methods 0.000 description 4
- 150000004767 nitrides Chemical class 0.000 description 3
- 229910001562 pearlite Inorganic materials 0.000 description 3
- 230000000704 physical effect Effects 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- 238000005096 rolling process Methods 0.000 description 3
- 239000007858 starting material Substances 0.000 description 3
- 229910000742 Microalloyed steel Inorganic materials 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
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- 150000001875 compounds Chemical class 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 230000000630 rising effect Effects 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 206010017472 Fumbling Diseases 0.000 description 1
- 229910000617 Mangalloy Inorganic materials 0.000 description 1
- 229910000954 Medium-carbon steel Inorganic materials 0.000 description 1
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
- QFGIVKNKFPCKAW-UHFFFAOYSA-N [Mn].[C] Chemical compound [Mn].[C] QFGIVKNKFPCKAW-UHFFFAOYSA-N 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 238000005261 decarburization Methods 0.000 description 1
- 238000007323 disproportionation reaction Methods 0.000 description 1
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Abstract
The invention discloses composition of medium-and high carbon micro-alloy non quenched and tempered steel. The medium-and high carbon micro-alloy non quenched and tempered steel comprises the following trace elements by the content in total mass: 0.060-0.220% of V, 0.010-0.030% of Ti and 0.020-0.030% of Nb. The invention also discloses a forging-cooling controlled technique method of the micro-alloy non quenched and tempered steel, for example, the method includes the following process: heating before forging, furnace exiting of the heating before forging, widening, preforging, final-forging,trimming cutting, hole extruding, furnace entering of cooling controlling after forging, cooling controlling, furnace exiting of cooling controlling after forging, and charging basket entering. The adoption of the technical proposal aims at producing products satisfying mechanical property by a temperature controlled cooling method without post heat treatment in the casting process.
Description
Technical field
The invention belongs to the technical field of metal material heat processing, relate to the middle carbon microalloy pearlitic steel control and forge---the control refrigeration technique more particularly, the present invention relates to a kind of medium high carbon middle carbon microalloy pearlitic steel.In addition, the control that the invention still further relates to this medium high carbon middle carbon microalloy pearlitic steel is forged---control cold processing method.
Background technology
The microalloy technology is the novel metallurgical subject that occurs the seventies in 20th century, is the important symbol that traditional Iron and Steel Production changes to modernized metallurgical production.
Microalloying forges and uses non-hardened and tempered steel, starts from the mid-1970s, at first in Germany, then develops in Sweden.China begins the research work of this respect at the beginning of the eighties.The strong carbide forming element of adding trace in the medium carbon steel, the control forging process, sedimentary separating out and grain refining controlled in the cooling after high temperature deformation when utilizing forging and the forging, thereby steel is strengthened.Make it just can satisfy the part requirement without reserve thermal treatment.For energy-saving and cost-reducing, middle carbon microalloy pearlitic steel is used to make on the moving parts of fatigue strength design requirements more and more, becomes the important symbol of weighing a national industrial development level simultaneously.At present, micro-alloyed steel accounts for the ratio of steel total amount, and world standard is 10%-15%, and industrialized country reaches about 30%, and China's less than 5%, therefore, the micro-alloyed steel non-hardened and tempered steel has become the important development direction of Iron and Steel Production.
Because this class high strength non-hardened and tempered steel manufacturing requirements height is difficult for grasping.Each position deflection differs in forging process, and temperature distributing disproportionation is even, and the austenite crystal distortion is complicated and changeable with the recrystallize tendency, and the easiest production mixed crystal and crystal grain are grown up unusually.Thereby hardening capacity produces uneven variation.Cause it in daily production, also to be in the stage of fumbling.It simultaneously also is the another one important factor of its development of restriction.
Summary of the invention
First problem to be solved by this invention provides a kind of medium high carbon middle carbon microalloy pearlitic steel, its objective is in forged process, by temperature controlled cooling method, does not need can produce the product that satisfies mechanical property through subsequent heat treatment.
To achieve these goals, the technical scheme taked of the present invention is:
This medium high carbon middle carbon microalloy pearlitic steel provided by the present invention is a major ingredient with Fe, and described medium high carbon middle carbon microalloy pearlitic steel comprises following composition: C:0.520%～0.730% according to the content in total mass; Si :≤0.850%; Mn:0.40%～0.90%; P≤0.045%; S :≤0.070%; Cr≤0.250%; Mo≤0.070%; Ni≤0.30%; Cu≤0.30%; Al :≤0.050%, it is characterized in that: described medium high carbon middle carbon microalloy pearlitic steel also comprises V, Ti and the Nb of trace.
Described V, Ti and the Nb content in total mass is respectively: V:0.060%～0.220%; Ti:0.010%～0.030%:Nb:0.020%～0.030%.
Second problem to be solved by this invention provides the control that is used for above-described medium high carbon middle carbon microalloy pearlitic steel and forges---and control cold processing method, its goal of the invention is identical with technique scheme.Described medium high carbon middle carbon microalloy pearlitic steel is C56E2, and described C56E2 is used to make wheel hub class part.Its technical scheme: described medium high carbon middle carbon microalloy pearlitic steel C56E2 comprises following composition: C:0.520%～0.730% according to the content in total mass; Si :≤0.850%; Mn:0.40%～0.90%; P≤0.045%; S :≤0.070%; Cr≤0.25%; Mo≤0.070%; Ni≤0.30%; Cu≤0.30%; Al :≤0.010%.
The control of described C56E2 is forged---and control cold processing method and comprise following process:
---heating is come out of the stove before forging, and---pier is thick, and---blocking------cut edge and---squeeze the hole and---forge that the back control is cold goes into stove---it is cold to forge the back control, and---forging cold the coming out of the stove of back control---goes into charging basket by finish-forging in heating before forging.
Control at described C56E2 is forged---and control in the process of cold processing method, the pass of described part temperature and time is: coming out of the stove with heating before forging is start time, then:
Temperature when heating is come out of the stove before forging is 1231 ℃;
To 0.25min, the temperature before pier is thick is 1150 ℃;
To 0.53min, the temperature before the blocking is 1090 ℃;
To 0.73min, the temperature behind the finish-forging is 1010 ℃;
To 0.90min, the temperature before cutting edge is 960 ℃;
To 1.17min, the temperature before the crowded hole is 912 ℃;
To 1.30min, the temperature of forging when the back control is cold goes into stove is 884 ℃;
To 5.30min, the temperature when forging cold the coming out of the stove of back control is 552 ℃;
To 7.30min, the temperature when going into charging basket is 454 ℃.
The part temperature of above-described day part, its deviation control is in ± 20 ℃.
The 3rd problem to be solved by this invention provides another control that is used for above-described medium high carbon middle carbon microalloy pearlitic steel and forges---and control cold processing method, its goal of the invention is identical with technique scheme.Described medium high carbon middle carbon microalloy pearlitic steel is C70, and described C70 is used to make connection rod of automobile engine class part.Its technical scheme: described medium high carbon middle carbon microalloy pearlitic steel C70 comprises following composition: C:0.670%～0.730% according to the content in total mass; Si:0.450%～0.850%; Mn:0.40%～0.70%; P≤0.045%; S :≤0.045%; Cr≤0.20%; Mo≤0.050%; Ni≤0.20%; Cu≤0.20%; Al :≤0.010%.
The control of described C70 is forged---and control cold processing method and comprise following process:
---heating is come out of the stove before forging, and------blocking------finish-forging---is cut edge and---is forged that the back control is cold goes into stove---it is cold to forge the back control, and---forging cold the coming out of the stove of back control---goes into charging basket by punching in roll forging in heating before forging.
Control at described C70 is forged---and control in the process of cold processing method, the pass of described part temperature and time is: coming out of the stove with heating before forging is start time, then:
Temperature when heating is come out of the stove before forging is 1236 ℃;
To 0.25min, the temperature during roll forging is 1147 ℃;
To 0.53min, the temperature before the blocking is 1093 ℃;
To 0.73min, the temperature behind the finish-forging is 1032 ℃;
To 0.90min, the temperature before the punching is 976 ℃;
To 1.17min, the temperature before cutting edge is 930 ℃;
To 1.30min, the temperature of forging when the back control is cold goes into stove is 901 ℃;
To 5.30min, the temperature when forging cold the coming out of the stove of back control is 580 ℃;
To 7.30min, the temperature when going into charging basket is 431 ℃.
The part temperature of above-described day part, its deviation control is in ± 20 ℃.
The present invention adopts technique scheme, adopt non-hardened and tempered steel to replace traditional modified heat-treated steel, can cancel modified (quenching and tempering) operation, simplify the technological process of production by rational temperature control process for cooling, improve material use efficiency, cut down the consumption of energy and manufacturing cost; Simultaneously can also reduce the deformation effect of repeatedly thermal treatment, improve part quality, obtain the performance of quenched and tempered steel, even surpass the performance of quenched and tempered steel part.Separate out in ferrite that microalloy element vanadium, titanium, niobium are formerly separated out with the form of tiny carbide, nitride and the perlite.These precipitates and parent phase keep the coherence relation, and steel is strengthened.Therefore adopt non-hardened and tempered steel on cost performance, to be far superior to quenched and tempered steel.
Description of drawings
Below expressed content of each width of cloth accompanying drawing of this specification sheets and the mark among the figure are made brief description:
Fig. 1 forges the cold temperature changing curve diagram of control for the control of the C56E2 among the present invention;
Fig. 2 forges the cold temperature changing curve diagram of control for the control of the C70 among the present invention;
Fig. 3 is the stress-strain curve diagram by the C56E2 part of processing method acquisition of the present invention;
Fig. 4 is the stress-strain curve diagram by the C70 part of processing method acquisition of the present invention;
Fig. 5 is (* 100) metallurgical microscopic by the C56E2 of processing method acquisition of the present invention;
Fig. 6 is (* 500) metallurgical microscopic by the C56E2 of processing method acquisition of the present invention;
Fig. 7 is the Decarburized layer microgram by the C70 of processing method acquisition of the present invention;
Fig. 8 is the core hardness distribution plan of the C56E2 of employing processing method acquisition of the present invention.
Fig. 9 is the hardness distribution of the C70 of employing processing method acquisition of the present invention.
Embodiment
Contrast accompanying drawing below, by description to exemplifying embodiment, to the specific embodiment of the present invention such as related material composition, effect and principle of work, manufacturing process and manipulate method etc., be described in further detail, inventive concept of the present invention, technical scheme had more complete, accurate and deep understanding to help those skilled in the art.
One, the material composition of medium high carbon middle carbon microalloy pearlitic steel and respective performances index:
This medium high carbon middle carbon microalloy pearlitic steel provided by the present invention is a major ingredient with Fe, and described medium high carbon middle carbon microalloy pearlitic steel comprises following composition: C:0.520%～0.730% according to the content in total mass; Si :≤0.850%; Mn:0.40%～0.90%; P≤0.045%; S :≤0.070%; Cr≤0.250%; Mo≤0.070%; Ni≤0.30%; Cu≤0.30%; Al :≤0.050%, it is characterized in that: described medium high carbon middle carbon microalloy pearlitic steel also comprises V, Ti and the Nb of trace.
Be that the present invention adopts V, the Ti of trace and the concrete exemplifying embodiment of Nb below:
Described V, Ti and the Nb content in total mass is respectively: V:0.060%～0.220%; Ti:0.010%～0.030%; Nb:0.020%～0.030%.
Cardinal principle of the present invention: non-hardened and tempered steel is to add micro alloying elements such as vanadium, titanium, niobium on the basis of medium high carbon manganese steel, in heat-processed, be dissolved in the austenite, because of the solid solubility of the vanadium in the austenite, titanium, niobium along with cooling reduces.Separate out in ferrite that microalloy element vanadium, titanium, niobium will formerly be separated out with the form of tiny carbide, nitride and the perlite.These precipitates and parent phase keep the coherence relation, and steel is strengthened.
Main advantage is: adopt non-hardened and tempered steel, replace traditional modified heat-treated steel, can cancel modified (quenching and tempering) operation, can simplify the technological process of production, improve material use efficiency, improve part quality, cut down the consumption of energy and manufacturing cost, simultaneously can also reduce the deformation effect of repeatedly thermal treatment, obtain quenched and tempered steel or surpass its performance part.Therefore adopt non-hardened and tempered steel on sexual valence, to be far superior to quenched and tempered steel.
Two, middle carbon microalloy pearlitic steel C56E2 (being used for the part on the automobile):
Medium high carbon middle carbon microalloy pearlitic steel provided by the invention adopts C56E2, is the starting material that are applied to the automotive hub forging as forging, and its shape all belongs to solid of revolution, security personnel's part, and its mechanical property requires as follows:
| 1. tensile strength | Greater than 900N/mm2 |
| 2. yield-point | Greater than 550N/mm2 |
| 3. unit elongation | Greater than 12% |
| 4. relative reduction in area | Greater than 25% |
| 5. hardness | HB 265-300 |
Its product requirement and characteristics thereof:
Grain fineness number requires: more than the level Four, under regular situation, this forging only under the situation of modified (quenching+tempering), could satisfy its mechanical property requirements.But, along with the development of microalloy technology, substitute by raw-material, select middle carbon microalloy pearlitic steel C56E2 for use, by rational process for cooling, just can reach and surpass the mechanical property requirement of quenched and tempered steel, also reduced production cost simultaneously.
To C56E2 raw-material require as follows:
Described medium high carbon middle carbon microalloy pearlitic steel C56E2 comprises following composition: C:0.520%～0.730% according to the content in total mass; Si :≤0.850%; Mn:0.40%～0.90%; P≤0.045%; S :≤0.070%; Cr≤0.25%; Mo≤0.070%; Ni≤0.30%; Cu≤0.30%; Al :≤0.010%.Control to other composition: O≤0.0015; As≤0.04; Sn≤0.03; Sb≤0.005; Pb≤0.002; Ca≤0.001; H
2≤ 0.0002.
Except requirement, be to raw-material other requirement to material composition:
1, physicals and mechanical property:
Rm N/mm
2≤859，HBW2.5/187.5≤255。
2, microstructure:
Unprocessed: ferrite and nodular troostite (allowing spheroidite).
3, autstenitic grain size:
7 grades or thinner, press DIN 50601/ASTM E 112 quench methods.
Because the mechanical property of non-hardened and tempered steel depends on the reinforcement of matrix microstructure and precipitated phase, therefore, in the non-hardened and tempered steel production process, how to accomplish effectively to control its speed of cooling, guarantee the cooling of part various piece simultaneously evenly, it is crucial obtaining satisfactory metallographic structure.
The matter steel design of non-accent steel mainly is divided into two parts: the microalloying element and control processing thermal treatment and the cooling CONTROL PROCESS thereof that promptly adopt Nb, V, Ti, B etc., its chemical ingredients is the internal factor of microalloying non-hardened and tempered steel performance, and its suitable hot-work is formulated, be that controlled rolling (forging), controlled chilling are the external conditions of guaranteed performance, after that is to say that the design of non-hardened and tempered steel composition is determined, its performance is by the regulation and control decision of hot-work condition, and this is our problem to be solved aborning just.
Cooling controlling and rolling controlling process comprises Heating temperature, finishing temperature, rolls postcooling speed, deformation degree and deformation rate etc. intensity, the toughness of non-hardened and tempered steel is had remarkable influence.
In sum, the invention provides the control that is used for above-described middle carbon microalloy pearlitic steel C56E2 forges, and---control cold processing method, the control of described C56E2 is forged---controlled cold processing method and comprised following process:
---heating is come out of the stove before forging, and---pier is thick, and---blocking------cut edge and---squeeze the hole and---forge that the back control is cold goes into stove---it is cold to forge the back control, and---forging cold the coming out of the stove of back control---goes into charging basket by finish-forging in heating before forging.
The temperature control furnace of this process using, its internal structure have three groups of blower fans and three groups of well heaters respectively.
For the C56E2 non-hardened and tempered steel, it mainly is to obtain the ferrite-pearlite tissue.Its heating is along with the rising of temperature, carbide and nitride dissolve in the austenite by the order of vanadium, niobium, titanium gradually, austenite crystal is grown up gradually, and this causes perlite percentage ratio after the phase transformation, pearlite colony diameter and cemetite lamellae thickness to increase, and ferrite grain size reduces.The microalloy element carbonitride that is dissolved in the austenite is separated out in process of cooling, and therefore along with the rising of Heating temperature, the intensity of steel increases, and plasticity and toughness reduce, and ductile-brittle transition temperature raises.
The speed of deflection and deformation increases can cause austenite crystal embrittlement or " elongation " more, the ferrite percentage is plain to be increased, ferrite and pearly-lustre group size reduce, tiny tissue rises intensity and toughness simultaneously. but in reality is produced, rate of deformation depends primarily on equipment, and deflection mainly depends on the complexity of part, concerning these, influence is less relatively for it, difficult the change.
Finishing temperature reduces, and austenite recrystallization is insufficient or be suppressed, and is organized as tiny ferrite crystal grain and perlite after the transformation.Yield strength and toughness improve.
Processing temperature and deformation quantity promptly have influence on recrystallize and austenite size, have influence on deformation again and bring out the degree of separating out, and processing temperature is too high, and recrystallize speed is fast, and austenite crystal is excessive, and cooling back intensity raises, and toughness descends; Processing temperature is low, and the recrystallize motivating force is little, and produces deformation and bring out and separate out, crystal grain thinning, and intensity improves, and particularly toughness improves bigger.Deformation quantity increases under same temperature, and intensity and toughness improve simultaneously.
Separate out precipitation strength and microstructure that the postcooling mode of rolling of perlite and ferrite non-hardened and tempered steel influences the micro alloying element compound change.Cooled off and caused precipitated phase and microstructure alligatoring slowly; Cold soon after the hot-work, perlite percentage ratio increases, ferrite grain size, perlite sheet spacing and the thick reduction of cemetite lamellae simultaneously, and intensity and toughness are improved; Cause bainite to occur but cool off too fast meeting, speed of cooling shows as the influence of precipitation strength: speed of cooling increases, and precipitate disperse degree increases, but when speed of cooling above behind the certain value, separate out insufficiently, reduce the precipitation strength effect on the contrary.Suitable speed of cooling will obtain the higher precipitated phase of small and dispersed degree and thinner ferrite and perlite rolls the back tissue.
In a word, for ferrite-pearlite type non-hardened and tempered steel, reduce Heating temperature and finish to gauge (forgings) temperature, increase deflection and deformation rate, speed of cooling all helps improving intensity and toughness faster.
Control at described C56E2 is forged---and control in the process of cold processing method, for the temperature control furnace of this process using, its internal structure has three groups of blower fans and three groups of well heaters respectively.As shown in Figure 1, the pass of described part temperature and time is: coming out of the stove with heating before forging is start time, then:
Temperature when heating is come out of the stove before forging is 1231 ℃;
To 0.25min, the temperature before pier is thick is 1150 ℃;
To 0.53min, the temperature before the blocking is 1090 ℃;
To 0.73min, the temperature behind the finish-forging is 1010 ℃;
To 0.90min, the temperature before cutting edge is 960 ℃;
To 1.17min, the temperature before the crowded hole is 912 ℃;
To 1.30min, the temperature of forging when the back control is cold goes into stove is 884 ℃;
To 5.30min, the temperature when forging cold the coming out of the stove of back control is 552 ℃;
To 7.30min, the temperature when going into charging basket is 454 ℃.
The part temperature of above-described day part, its deviation control is in ± 20 ℃.
Adopt the detected result after the above-mentioned technology:
A, stretching experiment detected result are: (mechanical property is qualified)
| Specimen shape | Round steel | Specimen size | 10 |
| Sample area (mm 2) | 78.54 | The original gauge length of sample (mm) | 50.0 |
| Gauge length/mm has no progeny | 57.46 | Extensometer gage length (mm) | 50 |
| Elongation after fracture/% | 14.92 | Relative reduction in area (%) | 47.29 |
| Tensile strength/MPa | 947.3 | The area (mm2) of having no progeny | 41.40 |
| Surrender strong/MPa | 642.3 |
B, metallographic detected result:
The metallurgical microscopic of the C56E2 that obtains by processing method of the present invention as shown in Figure 5 and Figure 6.Fig. 5 is * 100 times; Fig. 6 is * 500.The about 0.07mm of half Decarburized layer.
Metallographic structure: ferrite+perlite;
Grain fineness number: 6 grades.
C, stress-strain curve:
The stress-strain curve diagram of the C56E2 part that obtains by processing method of the present invention as shown in Figure 3.
D, exemplar core hardness:
The core hardness distribution plan that adopts the C56E2 that processing method of the present invention obtains as shown in Figure 8.
The hardness of each point is respectively:
a、HB 290；b、HB 285；c、HB 272；d、HB 292；e、HB 285。
Three, middle carbon microalloy pearlitic steel C70 (being used for the part on the automobile):
Medium high carbon middle carbon microalloy pearlitic steel provided by the invention adopts C70, is the starting material that are applied to connection rod of automobile engine as forging, belongs to security personnel's part, and its mechanical property requires as follows:
| 1. tensile strength | Greater than 850N/mm2 |
| 2. yield-point | Greater than 550N/mm2 |
| 3. unit elongation | Greater than 10% |
| 4. relative reduction in area | Greater than 20% |
| 5. hardness | HB 252-296 |
Its product requirement and characteristics thereof:
There is the decarburization requirement on the surface, the maximum 0.3mm of total decarburized layer, the maximum 0.1mm of full Decarburized layer.Forging has weight tolerance requirement 3.714Kg ± 120g.The forging ' s block dimension accuracy requirement is higher.Under regular situation, this forging only under the situation of modified (quenching+tempering), could satisfy its mechanical property requirements.But, along with the development of microalloy technology, substitute by raw-material, select middle carbon microalloy pearlitic steel C70 for use, by test, formulate rational temperature control process for cooling, just can reach and surpass the mechanical property requirement of quenched and tempered steel, also reduced production cost simultaneously.
To C70 raw-material require as follows:
Described medium high carbon middle carbon microalloy pearlitic steel C70 comprises following composition: C:0.670%～0.730% according to the content in total mass; Si:0.450%～0.850%; Mn:0.40%～0.70%; P≤0.045%; S :≤0.045%; Cr≤0.20%; Mo≤0.050%; Ni≤0.20%; Cu≤0.20%; Al :≤0.010%.
Except requirement, be to raw-material other requirement to material composition:
1, physicals and mechanical property:
No physical property energy and mechanical property requirement.
2, microstructure:
The starting material microstructure should be perlite and ferrite.
3, autstenitic grain size (GB/T6394):
Measure 4～8 grades of autstenitic grain sizes by China's standard method.
5, non-metallic inclusion grading:
I oxide compound (GB/T10561)≤4 grade;
Ii sulfide (GB/T10561)≤4 grade.
The invention provides another control that is used for above-described medium high carbon middle carbon microalloy pearlitic steel forges---and control cold processing method, its goal of the invention is identical with technique scheme.Described medium high carbon middle carbon microalloy pearlitic steel is C70, and described C70 is used to make connection rod of automobile engine class part.Its technical scheme is: as shown in Figure 2, the control of above-described C70 is forged---and control cold processing method and comprise following process:
---heating is come out of the stove before forging, and------blocking------finish-forging---is cut edge and---is forged that the back control is cold goes into stove---it is cold to forge the back control, and---forging cold the coming out of the stove of back control---goes into charging basket by punching in roll forging in heating before forging.
The temperature control furnace of this process using, its internal structure have three groups of blower fans and three groups of well heaters respectively.
Its ultimate principle that control is forged, control is cold, requirement are as previously mentioned.
Because in the production process, process for cooling is subjected to the influence of part shape bigger, the deformation quantity of its head and afterbody is different, and speed of cooling is also inhomogeneous, by technological test and checking repeatedly, draws its temperature control cooling curve as shown in Figure 2.That is: forge in the control of described C70---control in the process of cold processing method, the pass of described part temperature and time is: coming out of the stove with heating before forging is start time, then:
Temperature when heating is come out of the stove before forging is 1236 ℃;
To 0.25min, the temperature during roll forging is 1147 ℃;
To 0.53min, the temperature before the blocking is 1093 ℃;
To 0.73min, the temperature behind the finish-forging is 1032 ℃;
To 0.90min, the temperature before the punching is 976 ℃;
To 1.17min, the temperature before cutting edge is 930 ℃;
To 1.30min, the temperature of forging when the back control is cold goes into stove is 901 ℃;
To 5.30min, the temperature when forging cold the coming out of the stove of back control is 580 ℃;
To 7.30min, the temperature when going into charging basket is 431 ℃.
The part temperature of above-described day part, its deviation control is in ± 20 ℃.Adopt the detected result after the above-mentioned technology:
A, stretching experiment detected result are: (mechanical property is qualified)
| Specimen shape | Round steel | Specimen size | 10.05 |
| Sample area (mm2) | 78.54 | Original gauge length (the mm0 of sample | 49.56 |
| Gauge length/mm has no progeny | 58.28 | Extensometer gage length (mm) | 50 |
| Elongation after fracture/% | 16.56 | Relative reduction in area (%) | 51.49 |
| Tensile strength/MPa | 930.2 | The area (mm2) of having no progeny | 38.48 |
| Surrender strong/MPa | 664.0 |
B, Decarburized layer detect:
The Decarburized layer microgram of the C70 that obtains by processing method of the present invention as shown in Figure 7.
C, stress-strain curve:
The stress-strain curve diagram of the C70 part that obtains by processing method of the present invention as shown in Figure 4.
D, hardness:
The hardness distribution that adopts the C70 that processing method of the present invention obtains as shown in Figure 9.
Hardness is respectively HB263 and HB267.
In conjunction with the accompanying drawings the present invention has been carried out exemplary description above; obviously specific implementation of the present invention is not subjected to the restriction of aforesaid way; as long as adopted the improvement of the various unsubstantialities that method of the present invention design and technical scheme carry out; or design of the present invention and technical scheme are directly applied to other occasion without improving, all within protection scope of the present invention.
Claims (3)
1. a medium high carbon middle carbon microalloy pearlitic steel is a major ingredient with Fe, and described medium high carbon middle carbon microalloy pearlitic steel comprises following composition according to the content in total mass:
C：0.520％～0.730％；Si：≤0.850％；Mn：0.40％～0.90％；P≤0.045％；S：≤0.070％；Cr≤0.250％；Mo≤0.070％；Ni≤0.30％；Cu≤0.30％；Al：≤0.050％，
It is characterized in that:
Described medium high carbon middle carbon microalloy pearlitic steel also comprises V, Ti and the Nb of trace, and described V, Ti and the Nb content in total mass is respectively: V:0.060%～0.220%; Ti:0.010%～0.030%; Nb:0.020%～0.030%.
2. a control that is used for the described medium high carbon middle carbon microalloy pearlitic steel of claim 1 is forged---and control cold processing method, it is characterized in that:
Described medium high carbon middle carbon microalloy pearlitic steel is C56E2, and described C56E2 is used to make wheel hub class part, and described medium high carbon middle carbon microalloy pearlitic steel C56E2 comprises following composition according to the content in total mass:
C：0.520％～0.730％；Si：≤0.850％；Mn：0.40％～0.90％；P≤0.045％；S：≤0.070％；Cr≤0.25％；Mo≤0.070％；Ni≤0.30％；Cu≤0.30％；Al：≤0.010％；
Described control is forged---and control cold processing method and comprise following process:
---heating is come out of the stove before forging, and---pier is thick, and---blocking------cut edge and---squeeze the hole and---forge that the back control is cold goes into stove---it is cold to forge the back control, and---forging cold the coming out of the stove of back control---goes into charging basket by finish-forging in heating before forging;
Forge in described control---control in the process of cold processing method, the pass of part temperature and time is: coming out of the stove with heating before forging is start time, then:
Temperature when heating is come out of the stove before forging is 1231 ℃;
To 0.25min, the temperature before pier is thick is 1150 ℃;
To 0.53min, the temperature before the blocking is 1090 ℃;
To 0.73min, the temperature behind the finish-forging is 1010 ℃;
To 0.90min, the temperature before cutting edge is 960 ℃;
To 1.17min, the temperature before the crowded hole is 912 ℃;
To 1.30min, the temperature of forging when the back control is cold goes into stove is 884 ℃;
To 5.30min, the temperature when forging cold the coming out of the stove of back control is 552 ℃;
To 7.30min, the temperature when going into charging basket is 454 ℃;
The part temperature of above-described day part, its deviation control is in ± 20 ℃.
3. a control that is used for the described medium high carbon middle carbon microalloy pearlitic steel of claim 1 is forged---and control cold processing method, it is characterized in that:
Described medium high carbon middle carbon microalloy pearlitic steel is C70, and described C70 is used to make connection rod of automobile engine class part, and described medium high carbon middle carbon microalloy pearlitic steel C70 comprises following composition according to the content in total mass:
C：0.670％～0.730％；Si：0.450％～0.850％；Mn：0.40％～0.70％；P≤0.045％；S：≤0.045％；Cr≤0.20％；Mo≤0.050％；Ni≤0.20％；Cu≤0.20％；Al：≤0.010％；
Described control is forged---and control cold processing method and comprise following process:
---heating is come out of the stove before forging, and------blocking------finish-forging---is cut edge and---is forged that the back control is cold goes into stove---it is cold to forge the back control, and---forging cold the coming out of the stove of back control---goes into charging basket by punching in roll forging in heating before forging;
Forge in described control---control in the process of cold processing method, the pass of part temperature and time is: coming out of the stove with heating before forging is start time, then:
Temperature when heating is come out of the stove before forging is 1236 ℃;
To 0.25min, the temperature during roll forging is 1147 ℃;
To 0.53min, the temperature before the blocking is 1093 ℃;
To 0.73min, the temperature behind the finish-forging is 1032 ℃;
To 0.90min, the temperature before the punching is 976 ℃;
To 1.17min, the temperature before cutting edge is 930 ℃;
To 1.30min, the temperature of forging when the back control is cold goes into stove is 901 ℃;
To 5.30min, the temperature when forging cold the coming out of the stove of back control is 580 ℃;
To 7.30min, the temperature when going into charging basket is 431 ℃;
The part temperature of above-described day part, its deviation control is in ± 20 ℃.
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| CN102586559A (en) * | 2011-01-05 | 2012-07-18 | 南京工程学院 | Manufacture technology of high-toughness microalloyed non-quenched and tempered steel forging |
| CN102728754A (en) * | 2011-04-07 | 2012-10-17 | 江铃汽车股份有限公司 | Reinforced control cooling method for non-tempered steel forging |
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| JP5761116B2 (en) * | 2012-04-27 | 2015-08-12 | 新日鐵住金株式会社 | Wheel steel |
| CN102676931A (en) * | 2012-06-08 | 2012-09-19 | 沈冬杰 | Composite micro-alloy medium and high carbon steel |
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| JP6652020B2 (en) * | 2016-09-01 | 2020-02-19 | 日本製鉄株式会社 | High strength hot forged non-heat treated steel parts |
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| CN111633166B (en) * | 2020-05-28 | 2022-03-11 | 江苏龙城精锻集团有限公司 | Pre-cooling forging process for 38MnVS6 steel |
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