CN106282847A - A kind of remnant forging thermal quenching steel - Google Patents
A kind of remnant forging thermal quenching steel Download PDFInfo
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- CN106282847A CN106282847A CN201510281916.3A CN201510281916A CN106282847A CN 106282847 A CN106282847 A CN 106282847A CN 201510281916 A CN201510281916 A CN 201510281916A CN 106282847 A CN106282847 A CN 106282847A
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Abstract
A kind of remnant forging thermal quenching steel, its composition and quality % be: C 0.25～0.50, Si 0.15～0.40, Mn 0.50～1.80, P≤0.035, S≤0.05, Cr 0.01～1.30, Mo≤0.35, Al 0.02～0.04, N 0.006～0.012, Ti 0.02～0.05, B 0.0005～0.0035, remaining is Fe and inevitable impurity.The present invention can not only effectively refine the high temperature austenite crystal grain of forging, and significantly reduces hardening heat.
Description
Technical field
The invention belongs to structural alloy steel technical field, relate to a kind of remnant forging thermal quenching steel, it is particularly applicable to improve
Residual forging heat quenching process performance.
Background technology
The composition of quenched and tempered steel is usually the carbon steel of carbon containing 0.25%～0.5% or low-alloy steel and medium alloy steel, and contains
One or more alloying elements, have relatively low or medium alloying level, and in steel, alloys producing mainly carries
The quenching degree of Gao Gang and guarantee part obtain intended combination property after high tempering.Constitutional detail on all kinds of machines
Using quenched and tempered steel in a large number, be a most popular class steel in structural steel, wherein, most widely used quenched and tempered steel has chromium system
Quenched and tempered steel (such as 40Cr, 40CrSi), chromium manganese systems quenched and tempered steel (such as 40CrMn), chromium nickel system quenched and tempered steel (as 40CrNiMo,
37CrNi3A), boracic quenched and tempered steel etc..
Quenched and tempered steel forging normative heat treatment is to be cooled to room temperature or lower temperature at forging mostly, and overcooling austenite phase occurs
After change, reheat reaustenitizing, then quenching, high tempering by technological procedure.Remnant forging thermal quenching is then
Residuals temperatures direct quenching after utilizing forging process for fuel to shape.Comparatively speaking, residual forging heat quenching process eliminates forging
The reheating process of reaustenitizing, not only makes full use of residual forging heat, significantly saves the energy, and simplify forging
Part Technology for Heating Processing, shortens the production cycle.The extensively application of this technique can obtain significant economic benefit, is producing
Upper great application value.
It practice, residual forging heat quenching process is not used widely, its reason has two:
First, compared with reheating quenching, tempering forging, remnant forging thermal quenching forging, the original austenite grain of forging
During being formed at high temperature forging, lacking the recrystallization crystal grain thinning process of reaustenitizing, therefore crystal grain is thicker,
Overheated structure easily occurs.
Secondly, Forging Technology with forging and molding as main purpose because heating in the forging loading and unloading unstable, artificial,
The factors such as demoulding difficulty, forging temperature may 1250～950 DEG C of fluctuation, final forging temperature may 1150～
Significantly change between 800 DEG C, this original austenite grain degree fluctuation that certainly will cause forging and immediate quenching temperature mistake
The appearance of the problem such as low, the stability of impact forging quenching quality, occur that forging laser quenching hardened layer is deeply not enough, hardened layer
The most uneven, hardening break, quenching distortion are irregular, there is the quality such as too much non-martensite microstructure in quenching structure
Problem.
Chinese patent: publication No. is CN102383036A, date of publication is that the patent of invention on March 21st, 2012 is open
A kind of medium carbon alloy steel being applicable to remnant forging thermal quenching, the composition proportion of this steel alloy is: C:0.25～0.55%,
Si:0.20～0.60%, Mn:0.90～1.70%, Ti:0.08～0.25%, B:0.001～0.005%, P:
≤ 0.035%, S:0.01～0.07%, surplus is Fe and inevitable impurity.Although this steel alloy is applicable to forging
Make immediate quenching, but in its formula, the content of Ti is up to 0.08～0.25%, liquation TiN will certainly be rolled up and be mingled with
Thing, causes the fatigue of materials performance of preparation and the notable deterioration of cutting ability.
Summary of the invention
It is an object of the invention to overcome the problem of residual forging heat quenching process poor-performing present in prior art, it is provided that
A kind of remnant forging thermal quenching steel that can significantly improve residual forging heat quenching process performance.
For realizing object above, the invention provides techniques below scheme:
A kind of remnant forging thermal quenching steel, the composition of described steel and quality % thereof be: C 0.25～0.50, Si 0.15～
0.40, Mn 0.50～1.80, P≤0.035, S≤0.05, Cr 0.01～1.30, Mo≤0.35, Al 0.02～
0.04, N 0.006～0.012, Ti 0.02～0.05, B 0.0005～0.0035, remaining is that Fe is with inevitable
Impurity.
Compared with prior art, the invention have the benefit that
1, a kind of remnant forging thermal quenching of present invention steel by quality % of Ti, Al, N is respectively set as Ti 0.02～
0.05, Al 0.02～0.04, N 0.006～0.012, it is achieved that the combined microalloying of Ti, Al, N, is formed
The carbonitride such as TiN, AlN undissolved in high-temperature heating stage part, on the one hand, the most molten nitride can be formed greatly
The dispersoid particle of amount, stops the roughening of high temperature austenite crystal grain, on the other hand, the nitride meeting being solid-solution in austenite
Induce disperse educt by high temperature deformation, can reach the mesh of refinement high temperature austenite crystal grain in conjunction with thermal deformation recrystallization process
, above-mentioned effect makes when Forge Heating temperature is not higher than 1250 DEG C, and the original austenite grain of forging is narrower than 4 grades,
When final forging temperature is 1200 DEG C～950 DEG C, the original austenite grain of forging is narrower than 5 grades, reaches quenched and tempered steel and reheats tune
Grain size level after matter, is the most also not result in forging the significantly change of cost.Therefore, the present invention can effectively refine
The high temperature austenite crystal grain of forging.
2, a kind of remnant forging thermal quenching of the present invention steel quality % of C, Mn, Cr, Mo, B is controlled respectively at C 0.25～
0.50, Mn 0.50～1.80, Cr 0.01～1.30, Mo≤0.35, B 0.0005～0.0035, above-mentioned element is equal
Austenite region can be expanded, by controlling their content, the stability of austenite can be effectively improved, improve material
Quenching degree, make the CCT curve of steel move to right, the Ar3 of steel be down to 700 DEG C or lower temperature, therefore steel finish-forging
After hardening heat can as little as 750 DEG C or lower temperature, thus remnant forging thermal quenching temperature range is significantly increased,
Prevent at the quench-hardened case of regulation, ferrite or other non-martensite microstructures occurring because rate of cooling is not enough, the most not only subtract
Little or prevent instability or the impact to immediate quenching technology stability of the forging became uneven, the Er Qie great of Forging Technology
Width reduces quenching distortion.Therefore, present invention significantly reduces hardening heat.
Accompanying drawing explanation
Fig. 1 is the profile of wheel hub part.
Fig. 2 is that 1# steel grade, the high temperature austenite crystal grain of 2# steel grade are grown up distribution curve.
Detailed description of the invention
Below in conjunction with detailed description of the invention, the present invention is further illustrated.
A kind of remnant forging thermal quenching steel, the composition of described steel and quality % thereof be: C 0.25～0.50, Si 0.15～
0.40, Mn 0.50～1.80, P≤0.035, S≤0.05, Cr 0.01～1.30, Mo≤0.35, Al 0.02～
0.04, N 0.006～0.012, Ti 0.02～0.05, B 0.0005～0.0035, remaining is that Fe is with inevitable
Impurity.
Composition and the effect of steel of the present invention are as follows:
The present invention passes through Ti, Al, N combined microalloying, it is ensured that at the highest Forge Heating temperature (1250 DEG C)
The austenite grain boundary pinning that heating 30min is formed is in the most molten nitride, and crystal grain is narrower than 4 grades, to control forging local (not
Deformed area) maximum crystal grain, make major part forging there is not deformed district；Simultaneously so that on forging " deformation-
Dynamic recrystallization district ", Direct Air-Cooled after final forging temperature insulation 10min or forging, recrystallization austenite grain boundary pinning
In the most molten carbonitride and the carbonitride of deformation-induced precipitation, crystal grain is narrower than 5 grades, reaches to refine high temperature austenite brilliant
The purpose of grain.
C:C is that one can be effectively increased quenching degree, it is ensured that structural alloy steel has the most basic element of sufficient intensity.Its
Content is the lowest, and Ar3 is too high, easily separates out pro-eutectoid ferrite, causes cooling deficiency；Content is the highest, and plasticity and toughness drop
Low.For ensureing that material had both had higher intensity, there are again good plasticity and toughness simultaneously, its content is set as
0.25%～0.50%.
Si:Si is a kind of not only to have can ensure that the strength of materials but also as the effective element of deoxidation during steel smelting, too low Si contains
Measuring and will increase deoxidation cost when making steel, too high Si content then can dramatically increase decarburizing tendency, therefore by Si content
It is maintained at 0.15%～0.40%.
Mn:Mn is to improve quenching degree, expands the effective element of austenite region, also makes the S in steel with MnS simultaneously
Form fix, prevent the hot short element caused because of S.It is unable to reach lowest performance when its content is less than 0.5% to want
Ask, when content reaches 1.8%, will significantly postpone " ferrite-pearlite " phase transformation of overcooling austenite, and be greatly improved
Quenching degree, and higher Mn content there is no need for quenching degree, and the segregation of Mn can be caused to increase, and increase
Cost of alloy, therefore its upper limit is set as 1.80%.
P:P has the effect of solution strengthening, but is easily caused toughness and deteriorates, and therefore as control of deleterious element, the upper limit sets
It is 0.035%.
S:S is easily combined generation MnS non-metallic inclusion with Mn, can refine austenite crystal during high temperature forging
Grain, the beneficially raising of toughness, MnS is mingled with beneficially raising part machinability, but sulphide inculsion is easy
Cause stress to be concentrated, reduce mechanical property, therefore S upper content limit is set as 0.05%.
Cr:Cr can improve material quenching degree and obdurability, uses with Mn Match of elemental composition, and its content is less than 0.01%,
Not reaching effect, more than 1.30%, though remaining to improve material quenching degree, may reduce toughness, therefore the upper limit sets
It is 1.30%.
Mo:Mo can improve material quenching degree and obdurability, and Mo allows to exist, because of molybdenum-iron valency as residual elements in steel
Lattice are high, can dramatically increase material cost, therefore its content are set as≤0.35%.
Ti:Ti is a kind of strong carbide and nitride forming element, and preferentially N is combined generation TiN in steel, suitable
The Second Phase Particles of the acinous Dispersed precipitate that the Ti of amount is formed is in Forge Heating (heating-up temperature 1150 DEG C～1250 DEG C)
During pinning austenite grain boundary, stop growing up of high-temperature heating stage and Deformation recrystallization austenite crystal.Content mistake
Little, disperse second particle of formation is few, and Grain refinement is not notable, too high levels, easily generates liquation bulky grain TiN,
The effect of TiN crystal grain thinning can not be played.Therefore Ti content is set as 0.02～0.05% by the present invention.
Al: in order to reduce liquation TiN inclusion content, it is necessary to control Ti upper content limit, now solid according to [Ti] [N]
Solubility product, the TiN amounts of particles separated out during solid-state phase changes is for obtaining the austenite crystal required by deficiency.For
This needs compound interpolation other strong nitrogen, carbide formers.The present invention select cheap Al serve as this role.
Al is the main deoxidant element in steel, and Al remaining N in steel superfluous after completing deoxidation is combined generation AlN, forging
Make in heating process part not to be dissolved in austenite, with solid-state phase changes during the TiN that separates out jointly stop high temperature austenitic
Body crystal grain is grown up, and meanwhile, the AlN being solid-solution in austenite is at high temperature deformation process and deformation tailing edge austenite grain boundary more
Dissipate and separate out, postpone the carrying out of recrystallization, it is ensured that thermal deformation recrystallization Austenite Grain Refinement.For ensureing crystal grain thinning
Effect, avoid there is substantial amounts of non-metallic inclusion in steel has negative effect simultaneously to performance, and then ensures continuous casting process
Performance and cc billet surface quality, in the present invention, Al content is set as 0.02～0.04%.
N:N is that one of element often deposited by steel grade, have the strongest affinity with the unit such as Ti, Nb, Al, can be formed stable
Gap phase carbonitride, to the solid solution of carbonitride, separate out and play an important role, thus effectively stop austenite crystal
Grain roughening.In the present invention, the N content scope of design, calculate and experiment through design, can be with above-mentioned regulation content
Ti, Al formed disperse the most tiny nitride Second Phase Particles, turn avoid the volume that needs in steelmaking process
The cost that outer increase denitrification or nitrogen pick-up operation or measure cause increases, and the N of excess easily forms bubble in steel and dredges
Pine.In the present invention, N content is set as 0.006～0.012%.
B:B add medium and low carbon steel or in, in low-carbon alloy steel, segregation, on crystal boundary, can dramatically increase austenite steady
Qualitative, reduce Ar3, suppression pro-eutectoid ferrite or perlitic transformation, thus improve the quenching degree of steel.Its addition
Measure the least, but effect is very big, the most relatively cheap.B has two states, i.e. solid solution state and combined state in steel.B
When being only solid-solution in austenite, in austenite isothermal or temperature-fall period, segregation in crystal boundary, raising through hardening could be played
Property effect, be referred to as " effective boron ".Content is too small, and effective hydroboration is inconspicuous, too high levels, can cause on crystal boundary
The generation of boride so that the quenching degree of steel and toughness reduce.Therefore B content is set as 0.0005～0.0035%.
Embodiment 1:
A kind of remnant forging thermal quenching steel, the composition of described steel and quality % thereof be: C 0.25, Si 0.40, Mn 1.80,
P 0.025, S 0.03, Cr 0.01, Mo 0.2, Al 0.03, N 0.006, Ti 0.04, B 0.0035, its
Remaining is Fe and inevitable impurity.
Embodiment 2:
A kind of remnant forging thermal quenching steel, the composition of described steel and quality % thereof be: C 0.45, Si 0.25, Mn 1.10,
P 0.016, S 0.022, Cr 0.1, Mo 0.017, Al 0.035, N 0.0062, Ti 0.035, B 0.002,
Remaining is Fe and inevitable impurity.
Embodiment 3:
A kind of remnant forging thermal quenching steel, the composition of described steel and quality % thereof be: C 0.35, Si 0.30, Mn 0.50,
P 0.035, S 0.01, Cr 1.3, Mo 0.35, Al 0.02, N 0.008, Ti 0.02, B 0.0035, its
Remaining is Fe and inevitable impurity.
Embodiment 4:
A kind of remnant forging thermal quenching steel, the composition of described steel and quality % thereof be: C 0.50, Si 0.15, Mn 0.80,
P 0.01, S 0.05, Cr 0.6, Mo 0.05, Al 0.04, N 0.012, Ti 0.05, B 0.0005, remaining
For Fe and inevitable impurity.
For detecting the performance of above-described embodiment steel, with existing production steel (composition and quality % be: C 0.40, Si 0.27,
Mn 1.36, P 0.016, S 0.022, Cr 0.1, Mo 0.015, N 0.004, Ti 0.03, B 0.0006)
Steel as a comparison, carries out the trial-production of car hub part, wherein, warm and hot forging heating-up temperature by itself and embodiment steel simultaneously
Being 1200～1250 DEG C, thermal forging technology process is jumping-up-blocking-finish-forging-immediate quenching-temper, and warm and hot forging obtains
The profile of wheel hub part as it is shown in figure 1, measure gas not according to GB/T 6394 metal mean grain size assay method
Compare with after the grain size at position, the results are shown in Table 1:
Table 1
Discovery can be compared by upper table, after Al, Ti, N combined microalloying, remnant forging thermal quenching wheel hub part
Each position grain size is narrower than the immediate quenching wheel hub part of existing production material.
Having document to report, by adding niobium element energy fining austenite grains, the present invention selects to be combined with the middle carbon containing niobium
(composition and quality % be steel: C 0.40, Si 0.25, Mn 1.12, P 0.014, S 0.012, Cr 0.08, Mo
0.027, N 0.005, Ti 0.035, B 0.0002, Nb 0.04) carry out grain size and grow up Experimental Comparison, for just
In comparing, steel grade of the present invention numbering is set as, and 1#, compared steel steel grade numbering are set as 2#, high temperature austenite crystal grain
Result of the test of growing up distribution curve is shown in that Fig. 2, result show: in hot stage, the Austenite Grain Growth speed of 1# steel grade
Degree is significantly slower than 2# steel grade.
It addition, be the mechanical performance index testing steel of the present invention, the present invention is manufactured experimently into pitman arm, pre-after forge hot
Be cooled to different temperature and carry out Quenching Treatment, and after test after 640 DEG C of tempering, meet pitman arm metallurgy skill
Art requirement.The results are shown in Table 2.
Table 2
| Hardening heat | Rm | Rp0.2 | A | Z | KU2 | Grain size |
| 700℃ | 866 | 719 | 14.5 | 58.5 | 66 | 6.5-7 |
| 750℃ | 855 | 689 | 16.5 | 59 | 65 | 6.5 |
| 800℃ | 879 | 724 | 14.25 | 56 | 71 | 6.5 |
| 880℃ | 872 | 728 | 13.25 | 57.5 | 89 | 6.5 |
| 920℃ | 862 | 692 | 15.5 | 57.5 | 83 | 6.5 |
Claims (1)
1. a remnant forging thermal quenching steel, it is characterised in that:
The composition of described steel and quality % thereof be: C 0.25～0.50, Si 0.15～0.40, Mn 0.50～1.80, P≤0.035, S≤0.05, Cr 0.01～1.30, Mo≤0.35, Al 0.02～0.04, N 0.006～0.012, Ti 0.02～0.05, B 0.0005～0.0035, remaining is Fe and inevitable impurity.
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111876663A (en) * | 2020-06-19 | 2020-11-03 | 江阴兴澄特种钢铁有限公司 | Alloy structural steel plate for knitted panel and manufacturing method thereof |
| CN112981260A (en) * | 2021-02-08 | 2021-06-18 | 上海振华港机重工有限公司 | Container crane wheel steel, container crane wheel and preparation method of container crane wheel steel |
| CN113528937A (en) * | 2021-06-09 | 2021-10-22 | 南京钢铁股份有限公司 | Economical steel for hardware tools and manufacturing method thereof |
| CN115491605A (en) * | 2022-09-27 | 2022-12-20 | 东风商用车有限公司 | Bainite steel for hot forging, process, device and system for manufacturing hot forged parts |
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| JP2013151719A (en) * | 2012-01-25 | 2013-08-08 | Nippon Steel & Sumitomo Metal Corp | Rolled steel bar or wire rod for hot forging |
| CN104178613A (en) * | 2014-08-07 | 2014-12-03 | 山东金马工业集团股份有限公司 | Controllable cooling method for high-pressure common rail |
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| CN101283109A (en) * | 2005-10-07 | 2008-10-08 | 都美工业株式会社 | Process for manufacturing roller shell of lower running body of construction machine |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN111876663A (en) * | 2020-06-19 | 2020-11-03 | 江阴兴澄特种钢铁有限公司 | Alloy structural steel plate for knitted panel and manufacturing method thereof |
| CN111876663B (en) * | 2020-06-19 | 2022-01-14 | 江阴兴澄特种钢铁有限公司 | Alloy structural steel plate for knitted panel and manufacturing method thereof |
| CN112981260A (en) * | 2021-02-08 | 2021-06-18 | 上海振华港机重工有限公司 | Container crane wheel steel, container crane wheel and preparation method of container crane wheel steel |
| CN113528937A (en) * | 2021-06-09 | 2021-10-22 | 南京钢铁股份有限公司 | Economical steel for hardware tools and manufacturing method thereof |
| CN115491605A (en) * | 2022-09-27 | 2022-12-20 | 东风商用车有限公司 | Bainite steel for hot forging, process, device and system for manufacturing hot forged parts |
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Application publication date: 20170104 |