CN101484601A - Hot-pressed steel sheet member and process for production thereof - Google Patents

Hot-pressed steel sheet member and process for production thereof Download PDF

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Publication number
CN101484601A
CN101484601A CN 200780025075 CN200780025075A CN101484601A CN 101484601 A CN101484601 A CN 101484601A CN 200780025075 CN200780025075 CN 200780025075 CN 200780025075 A CN200780025075 A CN 200780025075A CN 101484601 A CN101484601 A CN 101484601A
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steel
hot
temperature
steel plate
pressed
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CN101484601B (en
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西畑敏伸
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Nippon Steel Corp
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Sumitomo Metal Industries Ltd
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Priority to JP2006131704 priority Critical
Priority to JP131704/2006 priority
Priority to JP144169/2006 priority
Priority to JP2006144169 priority
Application filed by Sumitomo Metal Industries Ltd filed Critical Sumitomo Metal Industries Ltd
Priority to PCT/JP2007/059415 priority patent/WO2007129676A1/en
Publication of CN101484601A publication Critical patent/CN101484601A/en
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    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/02Ferrous alloys, e.g. steel alloys containing silicon
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/04Ferrous alloys, e.g. steel alloys containing manganese
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/18Ferrous alloys, e.g. steel alloys containing chromium

Abstract

A hot-pressed steel sheet member which exhibits excellent toughness after quenching without any subsequent treatment and which has a tensile strength of 1.8GPa or above has a microstructure which has a prior austenite grain size of 10[mu]m or below and which contains spontaneously tempered martensite. The chemical composition of the steel sheet contains C: 0.26 to 0.45%, Mn+Cr: 0.5 to 3.0%, Nb: 0.02 to 1.0%, Ti in an amount satisfying the relationship:3.42N+0.001 = Ti = 3.42N+0.5, one or more of Si: 0.5% or below, Ni: 2% or below, Cu: 1% or below, V: 1% or below and Al: 1% or below, and, if necessary, one or more of B: 0.01% or below, Nb: 1.0% or below, Mo: 1.0% or below and Ca: 0.001 to 0.005%. The steel sheet is kept at a temperature ranging from the Ac3 point to (the Ac3 point + 100 DEG C) for at most 5 minutes, hot-pressed, and then quenched by cooling at a rate of the upper critical cooling rate or above to the Ms point and at an average cooling rate of 10 to 500 DEG C/sec from the Ms point to 150 DEG C.

Description

Hot-pressed steel sheet member and manufacture method thereof
Technical field
The present invention relates to by hot-pressed manufacturing, tenacity excellent and high-intensity steel plate member and the manufacture method thereof of tensile strength more than 1.8GPa.This steel plate member is suitable as the machine structural parts headed by body structure parts with automobile, bottom part etc.The manufacturing that the invention still further relates to this steel plate member is employed hot-pressed with steel plate and manufacture method thereof.
Background technology
In recent years, in order to improve the fuel efficiency of automobile, realize the high strength of employed steel, the effort that alleviates the weight of automobile is pushed into.Consequently, in the manufacturing of passing through the member that the steel-sheet extrusion molding carries out that on automobile, extensively utilizes, because the reduction of the extrusion molding that the increase of the intensity that is accompanied by steel plate makes the member of manufacturing complicated shape become difficult.Specifically, have because the ductility of steel plate reduces, cause that the resilience and the wall bending that produce in the high position fracture of degree of finish become big, the such problem of dimensional precision deterioration takes place.Therefore, especially at the high-intensity steel plate that has used the tensile strength that has more than the 780MPa and carry out in the manufacturing of parts difficulty by extrusion molding and be entangled with.
If do not utilize extrusion molding but utilize roller to be shaped, then can easily process high tensile steel plate.But roller is shaped and can only be applicable to the manufacturing that has same profile components with lengthwise direction, therefore can not utilize in the manufacturing of the member of the shape of complexity.
Propose as GB 1490535, in being called as in hot-pressed method of steel plate of extrusion molding through heating, soft and high ductility, so the shape of the complexity that can high dimensional accuracy ground be shaped because the pyritous steel plate becomes.And, carry out extrusion molding after the austenite territory by steel plate is heated to, and have to go to the toilet cold shaping product and quench at the metal die that is used for extrusion molding, thus in the shaping while of steel plate, can reach the high strength of the steel plate that brings because of martensitic transformation.
Open in the flat 10-96031 communique the spy, disclose a kind of preliminary shaping die quenching method, it is at room temperature with after the shape of the former material extrusion molding of steel plate for regulation, such molding of putting into the metal die that is used for being shaped is heated to the austenite territory and carries out chilling, carry out the high-strength of steel plate thus simultaneously
Above-mentioned hot-pressed method and preliminary shaping die quenching method can be reached the extrusion molding of steel plate and the high strength of extrusion molded article simultaneously.
, if the tensile strength of the molding after quenching reaches the above high strength of 1.8GP, then existing hot-pressed method (comprising preliminary shaping die quenching method), after the quenching the toughness of extrusion molded article insufficient, distinguish not reach realistic scale.In fact, also not knowing up to now has the example that has produced toughness high strength extrusion molded article good, more than the tensile strength 1.8GPa under hot-pressed state.
Therefore, existing hot-pressed in, for make tensile strength be more than the 1.8GPa can be practical extrusion molded article, just need be to hard-tempered extrusion molded article enforcement temper to improve its toughness.But, in hot-pressed, append that tempering process can be related on the point of operating efficiency and equipment that significant cost rises and for preferred.
Summary of the invention
The invention provides a kind of technology, the tempering after it need not quench just can realize that tenacity excellent and tensile strength are the above manufacturing through hot-pressed extrusion molded article of 1.8GPa.
According to the present invention, chemical constitution by suitable selection steel plate, and the hot-rolled condition when suitably controlling the steel plate manufacturing, and suitably thereafter cold rolling, annealing of control according to circumstances, hot dip alloyed heat-treat condition such as zinc-plated, the quenching conditions after hot-pressed by suitable control more then can be reached above-mentioned purpose in addition.
A side, the present invention is a kind of through hot-pressed steel plate member, it has following chemical constitution: C:0.26~0.45% in quality %, Mn+Cr:0.5~3.0%, Nb:0.02~1.0%, satisfy the Ti of the amount of following formula (1), Si:0~0.5%, Ni:0~2%, Cu:0~1%, V:0~1%, Al:0~1%, B:0~0.01%, Mo:0~1.0%, Ca:0~0.005%, with surplus essence be Fe and impurity, and, having old austenite median size is below the 10 μ m, the micro organization that contains automatic tempered martensite, and tensile strength is more than the 1.8GPa
3.42N+0.001≤Ti≤3.42N+0.5 …(1)
The Ti in the formula and the N meaning are the content (quality %) of this element in the steel, and N is contained as impurity in steel.
In the present invention, hot-pressed except being that steel plate is heated to austenite territory (Ac in advance 3More than the point) temperature after carry out again beyond the hot-pressed method on the narrow sense meaning of extrusion molding, also comprise carry out extrusion molding with the temperature lower (for example room temperature) than austenite territory after, in being used for the metal die of extrusion molding, molding is heated to the temperature in austenite territory again, and the preliminary shaping die quenching method of quenching.
Described chemical constitution, also can in quality % contain among following more than a kind or 2 kinds: Si:0.01~0.5%, Ni:0.01~2%, Cu:0.01~1%, V:0.01~1%, Al:0.01~1%, B:0.001~0.01%, Mo:0.01~1.0% and Ca:0.001~0.005%.
In described chemical constitution, among the P that comprises as impurity in the steel, S and the N more than a kind or 2 kinds, in preferred its content of quality % satisfy below the P:0.005%, below the S:0.005% and below the N:0.002%.
From the another side, the present invention is a kind of hot-pressed steel plate of using, its can make have above-mentioned chemical constitution, tensile strength more than 1.8GPa through hot-pressed steel plate member.
The present invention also provides a kind of manufacture method of hot-pressed steel plate member in addition, and it comprises following content: the steel plate that will have above-mentioned chemical constitution is at Ac 3Point is above, (Ac 3Point+100 ℃) after following temperature field keeps time below 5 minutes, implement hot-pressed to this steel plate, and make that to reach the speed of cooling that Ms orders be more than the upper critical cooling rate, and the average cooling rate that makes Ms o'clock to 150 ℃ is 10~500 ℃/second, so cools off through hot-pressed pyritous molding.
In first form, hot-pressed steel plate member can also be made by aforesaid preliminary shaping die quenching method.The content that the manufacture method of the steel plate member of this form comprises is, with than Ac 3The temperature that point is low, the steel plate that uses the metal die extrusion molding to have above-mentioned chemical constitution is to put into the state of this metal die through the steel plate of extrusion molding, at Ac 3Point is above, (Ac 3Point+100 ℃) following temperature field keeps the time below 5 minutes, makes then that to reach the speed of cooling that Ms orders be more than the upper critical cooling rate, and makes Ms o'clock to 150 ℃ average cooling rate be 10~500 ℃/second to cool off.The extrusion molding temperature of this form is typically room temperature.
The present invention also provides a kind of hot-pressed manufacture method with steel plate preliminary shaping die quenching method, the extrusion molding excellence that is particularly suitable for.This hot-pressed content that comprises with the manufacture method of steel plate is, heat supply is rolled after making the temperature that steel ingot with above-mentioned chemical constitution or steel billet reach 1050~1300 ℃, finish this hot rolling with 800~950 ℃ temperature, 500~700 ℃ temperature is batched the steel band that is obtained by hot rolling.
This hot-pressed manufacture method with steel plate also can also comprise following operation:
(1) launches the above-mentioned steel band that batches, this steel band is implemented de-scaling processing and cold rolling;
(2) with in above-mentioned (1) by cold rolling steel band, at (Ac 1Point+10 ℃) above, Ac 3After the following temperature field of point keeps more than 10 seconds, be cooled to 300~500 ℃ temperature field with 1~100 ℃/second average cooling rate, then with this steel band after 300~500 ℃ temperature field keeps 30 second~10 minute, 1~50 ℃/second average cooling rate is cooled to room temperature;
(3) with in above-mentioned (1) by cold rolling steel band, at (Ac 1Point-100 ℃) above, (Ac 1Point+30 ℃) after following temperature field kept 1~24 hour, be cooled to room temperature with 1~100 ℃/hour average cooling rate;
(4) launch the above-mentioned steel band that batches, this steel band implemented desquamation processing and molten zinc plating, then more than 500 ℃, Ac 1The following temperature field of point is implemented alloying thermal treatment to this steel band;
(5) with in above-mentioned (1) by cold rolling steel band, after 700~900 ℃ temperature fields are implemented annealing, be cooled to temperature below 500 ℃ with 1~60 ℃/second average cooling rate, this steel band is implemented molten zinc plating, and thereafter in 500 ℃~Ac 1The temperature field of point is implemented alloying thermal treatment; Perhaps
(6) steel band that is cooled to room temperature in above-mentioned (3) is implemented molten zinc plating, and thereafter in 500 ℃~Ac 1The temperature field of point is implemented alloying thermal treatment.
So, the hot-pressed steel plate of using of the present invention comprises hot-rolled steel sheet, cold-rolled steel sheet, is the alloy galvanized steel plate of base material through heat treated cold-rolled steel sheet with hot-rolled steel sheet or cold-rolled steel sheet.
According to the present invention, need not carry out tempering, just can be manufactured on tenacity excellent, tensile strength under hot-pressed and the Annealed Strip at this moment is the above high strength hot-pressed steel sheet member of 1.8GPa.Consequently, can significantly reduce the manufacturing cost of utilizing hot-pressed high-strength steel board member.
Description of drawings
Fig. 1 is the explanatory view of the shape of the critical cooling velocity test film of measuring usefulness.
Fig. 2 is the TEM photo of the micro organization of expression hot extrusion steel plate member of the present invention.
Fig. 3 is the explanatory view of the model utility of cap moulding method.
Embodiment
Below illustrate in greater detail the present invention.In the explanation afterwards, about " % " all expressions " quality % " of the composition of steel plate and plating.
The chemical constitution of light plate of the present invention is as follows.
C:0.26~0.45%
C is the hardenability that improves steel plate, and mainly is the very important element of intensity (post-quenchingstrength) after decision is quenched.For in the high strength that reaches after the quenching more than the tensile strength 1.8GPa, making C content at least is 0.26%.On the other hand, if C content surpasses 0.45%, the intensity of the steel plate after then quenching is too high, and its toughness deterioration is remarkable.Preferred C content is 0.28~0.33%.
Mn+Cr:0.5~3.0%
Mn and Cr are improving the hardenability of steel plate, and are unusual effective elements on stable intensity after obtaining high quenching.When being lower than 0.5%, this effect is insufficient when the total content (hereinafter referred to as " (Mn+Cr) content ") of Mn and Cr.On the other hand, if (Mn+Cr) content surpasses 3.0%, then this effect is saturated, and stable intensity is guaranteed difficulty on the contrary.Preferably (Mn+Cr) content is 0.8~2.0%.
Nb:0.02~1.0%
The effect that Nb has is that steel plate is being heated to Ac 3When point is above, suppresses to recrystallize, and form fine carbide, thereby make austenite crystal become particulate, improve the toughness of the steel plate after quenching thus greatly.Contain the Nb more than 0.02% in order positively to obtain this effect.But if Nb content surpasses 1.0%, then the above-mentioned effect of Nb is saturated, and causing cost in vain increases.Preferred Nb content is 0.03~0.5%, more preferably 0.04~0.15%.
Ti: satisfy (1) formula (amount of 3.42N+0.001≤Ti≤3.42N+0.5)
The effect that Ti has is that steel plate is being heated to Ac 3When point is above, suppresses to recrystallize, and form fine carbide, thereby make austenite crystal become particulate, improve the toughness of the steel plate after quenching thus greatly.Make Ti content (%) for more than (3.42N+0.001) for the effect of positively bringing into play Ti.N is contained as impurity in steel.It is 0% also passable that N is essentially.On the other hand, if Ti content (%) surpasses (3.42N+0.5), then the above-mentioned effect of Ti is saturated, and causing cost in vain increases.Preferred Ti content is for satisfying (the amount of 3.42N+0.02≤Ti≤3.42N+0.08).
Si:0~0.5%、Ni:0~2%、Cu:0~1%、V:0~1%、Al:0~1%
These elements are to add element arbitrarily, but are all improving the hardenability of steel plate, and stable reaching after the high quenching on the intensity effectively, therefore preferably contain it more than a kind or 2 kinds.This effect of these elements is remarkable more than Si:0.01%, more than the Ni:0.01%, more than the Cu:0.01%, more than the V:0.01%, when Al:0.01% is above.But, containing each element and reach it more than higher limit, above-mentioned effect is still little, and causes the cost increase in vain, so the content of each element is above-mentioned scope.Preferred content when adding this element more than a kind or 2 kinds is Si:0.02~0.4%, Ni:0.02~1%, Cu:0.02~0.8%, V:0.02~0.5%, Al:0.01~0.1%.
B:0~0.01%
B adds element arbitrarily.It is improving the hardenability of steel plate, and obtains after the high quenching on the intensity effectively stable.In addition, B improves grain-boundary strength at grain boundary segregation, has the effect that the toughness of the steel plate after the quenching of making improves, and the austenite crystal during its heating is grown up in addition, and to suppress effect also high.These effects are 0.001% remarkable when above at B content.But if B content surpasses 0.01%, then these effects are saturated, and cause the cost increase.The preferred B content that B is contained sometimes is 0.001~0.01%, more preferably 0.001~0.0030%.
Mo:0~1.0%
Mo adds element arbitrarily.Its effect that has is that steel plate is being heated to Ac 3Point is when above, forms fine carbide and makes austenite crystal become particulate, so can improve the toughness of the steel plate after the quenching greatly.These effects are 0.01% remarkable when above at Mo content.But if Mo content surpasses 1.0%, then its effect is saturated, and causing cost in vain increases.The preferred L o content that Mo is contained sometimes is 0.01~1.0%, more preferably 0.04~0.20%.
Ca:0~0.005%
Ca adds arbitrarily element, has the inclusion miniaturization that makes in the steel, the effect that the toughness of the steel plate after the quenching is improved.These effects are 0.001% remarkable when above at Ca content.But if Ca content surpasses 0.005%, then its effect is saturated.Therefore, the preferred Ca content that Ca is contained sometimes is 0.001~0.005%, more preferably 0.002~0.004%.
The surplus of chemical constitution is made of Fe and impurity in essence.Impurity comprise non-metallic element that P, S, N are such and above-mentioned beyond metallic element.Wherein, the content of P, S, N is preferably as follows.
Below the P:0.005%
P is the toughness element of deterioration significantly that makes the steel plate after the quenching, therefore is preferably below 0.005%.More preferably below 0.003%.
Below the S:0.005%
S is the toughness element of deterioration significantly that makes the steel plate after the quenching, therefore is preferably below 0.005%.More preferably below 0.003%.
Below the N:0.002%
N forms inclusion in steel, be the element that makes the toughness deterioration of the steel plate after the quenching, therefore is preferably below 0.002%.More preferably below 0.001%.
At least a kind of content of preferred P, S, N as mentioned above.The content of remaining impurity element also can surpass the above-mentioned upper limit, but whole content of P, S, N is particularly preferably in below the above-mentioned upper limit.
Of the present invention through hot-pressed steel plate member, having tensile strength is the above high strength of 1.8GPa.This tensile strength is reached by the quenching behind extrusion molding in hot-pressed operation.Quench and in being used for hot-pressed metal die, carry out usually, but be not limited to this.
As described above, such is high-intensity through hot-pressed steel plate member, because the remarkable deterioration of toughness meeting in the past, so can not be for practical.Of the present invention through hot-pressed steel plate member, in order to reach this high strength such more than 1.8GPa, reach good toughness simultaneously, and have old austenite median size be the following such crystal grain of 10 μ m by miniaturization micro organization.Old austenite median size is preferably below the 8 μ m, more preferably below the 4 μ m.Old austenite median size exists with ... the heating condition (keeping temperature and hold-time) before hot-pressed and changes as described below.
According to the present invention, carry out hot-pressedly for steel plate with above-mentioned chemical constitution, but the heating condition (keep temperature and hold-time) before this moment hot-pressed is as follows.
In hot-pressed operation, in order to obtain intensity and toughness by quenching as target, and at Ac 3Point is above, (Ac 3Point+100 ℃) the following and temperature field time of steel plate below 5 minutes of keeping the heat supply extrusion molding.Why make and maintain the temperature at Ac 3More than the point, be in order to make organizing of steel become austenite one phase earlier, obtain intensity as target by quenching.Keeping the upper limit of temperature and the upper limit of hold-time, is for the old austenite particle diameter after will quenching is suppressed at below the 10 μ m, and above intensity also can be reached good toughness even the tensile strength of steel plate is 1.8GPa.Keep temperature to surpass (Ac if make 3Point+100 ℃) or the hold-time surpass 5 minutes, then old austenite crystal becomes more than the 10 μ m, can not obtain good toughness after quenching.Preferred maintenance temperature is Ac 3Point is above, (Ac 3Point+50 ℃) below, the preferred hold-time is below 2 minutes.Also have because old austenite particle diameter particulate more for preferred, so the lower limit of hold-time does not have special stipulation.
The hot-pressed use metal die that also comprises of the present invention, itself is not particularly limited.Hot-pressedly carry out again after preferably heating steel plate in advance, implement but also can follow aforesaid preliminary shaping die quenching method with above-mentioned condition.At this moment, carry out under these conditions being got final product by the heating of preformed molding.
When adopting preliminary shaping die quenching method, with than Ac 3The low temperature of point is carried out extrusion molding, will put into the state of metal die through the steel plate of extrusion molding, at Ac 3Point is above, (Ac 3Point+100 ℃) following temperature field keeps the time below 5 minutes, makes then that to reach the speed of cooling that Ms orders be more than the upper critical cooling rate, and makes Ms o'clock to 150 ℃ average cooling rate be 10~500 ℃/second to cool off.Extrusion molding in the preliminary shaping die quenching method carries out with room temperature usually, compares Ac but also can extrusion molding be heated to 3The steel plate of the temperature that point is low.
The cooling conditions and the method for cooling of quenching that is used for hot-pressed operation (comprising preliminary shaping die quenching method) is as follows.
In order to obtain also improving toughness a little when tensile strength is intensity more than the 1.8GPa, importantly not making by the micro organization after the quenching of the hot-pressed steel plate member that obtains becomes the complete martensitic stucture that in fact only is made of martensite, but becomes the tissue that also comprises automatic tempered martensite.
So-called tempered martensite automatically, be not carry out being used for tempered thermal treatment, but the tempered martensite that generates in the cooling when quenching, explanation in paddy open country, Suzuki work " science of iron steel-be condensed into the technology of iron " interior the Tian Laohe garden for example, (2001) 100 pages in Tokyo.Tempered martensite is to separate out fine cementite in lath, can distinguish with complete martensitic phase.
Under the situation of steel plate with above-mentioned chemical constitution, the micro organization of containing automatic tempered martensite, it can obtain in the following way: making the speed of cooling when quenching is upper critical cooling rate, make and reach the Ms point and can not spread phase transformation, thereafter, making the average cooling rate of Ms o'clock to 150 ℃ temperature range is 10~500 ℃/second.From Ms o'clock to 150 ℃ preferred average cooling rate was 15~200 ℃/second.
If arrive the Ms point in cooling light plate temperature, then the phase transformation heating that is brought by martensitic transformation takes place, but the thermal value of this phase transformation is very big.As above-mentioned, though it is slower than arriving the speed of cooling that Ms orders from the average cooling rate of Ms o'clock to 150 ℃ temperature range, but if so that the following cooling of Ms point with until reaching the identical method of cooling enforcement of Ms point, then because of the huge phase transformation heating of ordering, so the situation that can not reach the speed of cooling that needs is arranged at Ms.In this case, need carry out byer force than reaching the cooling that Ms orders, be preferably as follows described mode specifically from Ms o'clock to 150 ℃ cooling.
In hot-pressed method, normally in the steel metal die of the temperature of normal temperature or about tens of ℃, carry out extrusion molding, becoming cooling by metal die thus.Speed of cooling can change the thermal capacitance of metal die by changing metal die size (for example thickness), thereby makes it to change.By the metal die material being become different metal (for example copper etc.) speed of cooling is changed in addition.When not changing the size of metal die and material, change cooling water inflow, also can change cooling temperature by the metal die that uses water-cooling type.In addition, use the metal die that is cut with number place groove in advance, in extrusion molding, make the water that circulates in this groove, also can change speed of cooling thus, and by in the extrusion molding way, improving extrusion moulding machine, water is flowed also can change speed of cooling.In addition, change metal die gap (clearance), make it to change, also can change speed of cooling with the contact area of steel plate.
As the method that changes speed of cooling before and after the Ms point, for example thinking has following method.
(1) after arriving the Ms point, moves to immediately in the metal die of different metal die of thermal capacitance or room temperature state, thereby change speed of cooling;
(2) under the situation of water-cooled metal mould, after arriving the Ms point, the cooling water inflow of metal die is changed and the change speed of cooling;
(3) after arriving the Ms point, the water that circulates between metal die and molding immediately changes by making its water yield, thereby changes speed of cooling.
The mode of the shaping of hot-pressed method of the present invention is not particularly limited, if but illustration then has bending machining, draw forming, stretch forming, ream forming, flange to be shaped.Extrusion molding can be according to suitable selection of kind as the steel plate member of purpose.As the typical example of hot-pressed steel plate member, can enumerate as automobile with the car door anti-collision bar of strengthening part and bumper reinforcement etc.The manufacture method of steel plate member of the present invention, if being shaped simultaneously or having the means of cooling metal sheets after being shaped, then also can be applicable to extrusion molding moulding method in addition, for example roller is shaped.
Steel plate member of the present invention is also keeping good toughness.As can standing practical flexible level, the pendulum impact value under-120 ℃ is preferably 30J/cm 2More than.
Hot-pressed steel plate member, common is the purpose that descaling removes and handles by shot-peening.In this shot peening, because there is pair surface to import the effect of stress under compression, be suppressed, and fatigue strength improves such advantage so have delayed fracture.
In hot-pressed, steel plate is heated to the austenitic temperature territory and is subjected to austenite phase transformation.Therefore, the preliminary shaping die quenching method low with the extrusion molding temperature is different, and at room temperature the characteristic of machinery of steel plate is inessential before its heating, does not therefore have special stipulation for the kind of steel plate and the micro organization before the heating.That is, hot-pressedly no matter use which kind of of hot-rolled steel sheet, cold-rolled steel sheet (fully hard material full hard, annealing material), plated steel sheet can with steel plate.In addition, its manufacture method also is not particularly limited.As plated steel sheet, can enumerate aluminium is that plated steel sheet (for example fusion Aludip, fusion 55%Al-Zn alloy plated steel sheet), zinc are plated steel sheet (for example plating or hot-dip galvanized steel sheet, fusion 5%Al-An plated steel sheet, alloy galvanized steel plate, Ni-Zn alloy plating steel plate) etc.
On the other hand, to carry out the so hot-pressed method of preliminary shaping die quenching method of extrusion molding than the low temperature of room temperature or austenite territory, the steel plate of heat supply extrusion molding is preferred soft as far as possible in advance.For example, for hot-rolled steel sheet with implemented that preferred tensile strength is below the 780MPa the cold-rolled steel sheet of continuous annealing, preferred tensile strength is 780~1180Mpa for the steel plate of Cold Rolled Strip, and preferred tensile strength is below the 590MPa for the cold-rolled steel sheet of having implemented pack annealing.Be used to obtain the suitable manufacture method of so soft steel plate such as following.
Hot rolling
Implement hot rolling and become steel band after the temperature that makes steel ingot with above-mentioned chemical constitution or steel billet reach 1050~1300 ℃.Hot rolling finishes with 800~950 ℃ temperature, batches the steel band that obtains with 500~700 ℃ temperature.
Why making steel ingot or steel billet is 1050~1300 ℃, is the abundant solid solution of non-metallic inclusion for order processibility deterioration.This effect could confirmed more than 1050 ℃ for the steel plate of above-mentioned composition.And reach more than 1300 ℃, not only effect is saturated, and the oxide skin loss increases.More preferably 1050~1250 ℃ of this temperature, more preferably 1050~1200 ℃.
Make temperature reach 1050~1300 ℃ method for hot rolled steel ingot or steel billet, not only comprise heating to be lower than 1050 ℃ steel ingot or steel billet and reach 1050~1300 ℃ situation, also comprised the steel ingot that do not make after the continuous casting or the steel billet behind the split rolling method and be reduced to and be lower than 1050 ℃ and for the hot rolled situation.
Do not make the hot rolling end temp compare Ar 3Point is low.If with than Ar 3The temperature that point is low is implemented rolling, and it is remaining then to process ferrite, and ductility is deterioration significantly.If these problems then can not take place with more than 800 ℃ in the steel plate hot rolling end temp of above-mentioned chemical constitution.On the other hand, if the hot rolling end temp is high than 950 ℃, then there is the situation of the surface imperfection that generation oxide skin is pressed into etc.Therefore, making the hot rolling end temp is 800~950 ℃.
If coiling temperature is low excessively, then perlite, bainite, the so a large amount of generations of low temperature phase change tissue of martensite, ferritic structure reduces, so armor plate strength becomes too high.Therefore make the following of coiling temperature be limited to 500 ℃.On the other hand, if coiling temperature is too high, oxide skin thickening then, the de-scaling difficult treatment, so coiling temperature on be limited to 700 ℃.Batch turbid more preferably 550~650 ℃.
The hot rolled strip of making like this, for in preliminary shaping die quenching method, obtain good plasticity with hot-rolled state in the extrusion molding under the room temperature of typicalness, as the ferritic tissue that contains in volume fraction more than 50%, tensile strength is preferably below the 780MPa.The surplus of tissue can contain more than a kind or 2 kinds of perlite, bainite, martensite and retained austenite.It is that carbide and Ti system, Nb system, Mo system, Cr system, V are, Mn is a carbide that ferrite also can contain the such Fe of cementite.From the viewpoint of plasticity, low strength is more for preferred for steel band intensity, but based on the cost face be easy to the such point of intensity adjustment, then intensity is preferably more than the 590MPa, more preferably more than the 690MPa.
For after hot rolling, being batched and put cold steel band, after launching, can utilize pickling, shot-peening, grinding etc. more than a kind or 2 kinds usually, carry out remove (de-scaling) of the oxide skin of surface generation and handle.
Cold rolling
As above-mentioned when being used for extrusion molding as the steel band of Cold Rolled Strip for implement cold rolling through the hot rolled steel band, in order in utilizing preliminary shaping die quenching method hot-pressed, to obtain good plasticity, as the ferritic tissue that contains in volume fraction more than 50%, tensile strength is preferably below the 1180MPa.The intensity of cold-rolled steel strip is low more from the viewpoint of plasticity to be preferred more, but based on the cost face be easy to the such point of intensity adjustment and more than the preferred 780MPa.The tensile strength of cold-rolled steel strip is preferably 780~1100Mpa, more preferably the scope of 780~1050Mpa.Draft when cold rolling is preferably 30~80%, and more preferably 40~70%.
Method for annealing
As the annealing of above-mentioned cold rolling steel band, the continuous annealing of carrying out with deployed condition and coil into web-like and carry out pack annealing and all can.
When cold-rolled steel strip is implemented continuous annealing, anneal in the following way: be heated to (Ac 1Point+10 ℃) above, Ac 3Below the point, after more than this temperature field kept for 10 seconds, be cooled to 300~500 ℃ temperature field with 1~100 ℃/second average cooling rate, keep 30 seconds to more than 10 minutes at 300~500 ℃ temperature field again, be cooled to room temperature with 1~50 ℃/second average cooling rate thereafter.
If Heating temperature at this moment is than (Ac 1Point+10 ℃) low, then recrystallize can't fully carry out, and the intensity of steel plate uprises easily.On the other hand, if Heating temperature compares Ac 3Point is high, then generates the low temperature phase change phase easily owing to austenite one phaseization causes in cooling, and the intensity of steel band still uprises easily.If the hold-time after the heating is shorter than 10 seconds, then residual as the segregation of the Mn of substitutional element etc., the micro organization's heterogeneity after the annealing.And long-time heating can be caused the cost increase in vain, and therefore the hold-time after the heating was preferably below 300 seconds.The preferred non-oxidizing atmosphere of annealing atmosphere (98 volume %N for example 2+ 2 volume %H 2).
If the average cooling rate during annealing is too fast, then low temperature phase change generates mutually in a large number, and ferrite reduces, and steel band intensity uprises.On the other hand, if average cooling rate is slow excessively, then production efficiency reduces.Preferred average cooling rate is 1~20 ℃/second, more preferably 1~10 ℃/second.
Why making cooling stop temperature field is 300~500 ℃, is in order to suppress the generation of low temperature phase change phase as far as possible.Cooling stops temperature field and is preferably 300~500 ℃, more preferably 400~450 ℃.Why stopping temperature field in cooling and kept 30 seconds~10 minutes, is in order to promote the not ferrite transformation of transformed austenite.This hold-time is preferably 30 seconds~and 5 minutes, more preferably 30 seconds~3 minutes.Afterwards, steel band is cooled to room temperature with 1~50 ℃/second average cooling rate.If average cooling rate at this moment is faster than 50 ℃/second, then low temperature phase change generates mutually in a large number, and steel band intensity uprises.On the other hand, if average cooling rate is slower than 1 ℃/second, then production efficiency reduces.Preferred average cooling rate is 1~10 ℃/second.
Batch when carrying out pack annealing after the cold-rolled steel strip, at (Ac 1Point-100 ℃) above, (Ac 1Point+30 ℃) following temperature field keeps being cooled to room temperature with 1~100 ℃/hour average cooling rate after 1~24 hour, anneals thus.If keep temperature than (Ac 1Point-100 ℃) low, then the tensile strength of steel band can't fully reduce.On the other hand, if keep temperature than (Ac 1Point+30 ℃) height, then solid solution-the reverse transformation again of cementite excessively carries out, and generates the low temperature phase change phase in process of cooling thereafter, and the tensile strength of steel band becomes too high.Hold-time, the intensity of steel band reduced insufficient when being lower than 1 hour, and the hold-time also is saturated above 24 hours its effects, causes the waste of the energy in vain.In the process of cooling after annealing, if speed of cooling is fast, then low temperature phase change generates mutually, therefore as far as possible slowly more for preferred.But if slow excessively, then cause the reduction of processing efficiency, so speed of cooling is 1~100 ℃/hour, is preferably 1~50 ℃/hour.
The furnace atmosphere of pack annealing is preferably sneaking into of nitrogen to be lacked, and dew point is low as far as possible, contains the above gas of hydrogen 95 volume %.
What so obtain has implemented the annealed cold-rolled steel strip after cold rolling, in order in utilizing preliminary shaping die quenching method hot-pressed, to obtain good plasticity, as the ferritic tissue that contains in volume fraction more than 50%, the tensile strength of steel band is preferably below the 780MPa when continuous annealing, is preferably below the 590MPa during pack annealing.The tensile strength of steel band is low more to be preferred more, but based on the cost face be easy to the such point of intensity adjustment, no matter is under the situation of which kind of annealing method, all is preferably more than the 440MPa.
Molten zinc plating
Molten zinc plating all can be implemented the steel band of hot rolled strip, cold-rolled steel strip, cold rolling after annealing.From the viewpoint of manufacturing cost, molten zinc plating preferably carries out with the continuous fusion galvanizing line.Common continuous fusion galvanizing line disposes process furnace, cooling zone, fused zinc coating bath, alloying furnace continuously.At this, will impact the micro organization of steel band, preferably creating conditions of each stage set forth.
When the cold-rolled steel strip of Cold Rolled Strip was implemented annealing, preferably making annealing temperature was 700~900 ℃.Under than 700 ℃ of low temperature, recrystallize can't fully carry out, and the intensity of steel band uprises easily.On the other hand, under than 900 ℃ of high temperature, because austenite one phaseization causes that the generation temperature is mutually covert easily in the cooling, the intensity of steel band still uprises easily.For hot rolled strip with implemented the annealed cold-rolled steel strip and do not need to implement annealing originally.But, from the viewpoint of the operation of continuous fusion galvanizing line, because make Heating temperature become remarkable low temperature difficulty, so preferably carry out heating in the common scope of work.At this moment, for above-mentioned reason, preferably making maximum heating temperature is below 900 ℃.
Cool off steel band in order to implement molten zinc plating from annealing temperature or maximum heating temperature.This cooling is preferably 1~60 ℃/second up to the average cooling rate of the temperature field below 500 ℃.If cooling is too fast, then low temperature phase change generates mutually in a large number, and ferrite reduces and the intensity of steel band becomes too high.On the other hand, slow as if cooling off, then production efficiency reduces.
Molten zinc plating is followed ordinary method, and dipping steel band and picking up gets final product in containing fused zinc or the zinc alloy coating bath of (for example containing the zinc alloy to 5% Al).The control of plating adhesion amount is according to picking up speed and being undertaken by the flow adjustment of wiping away gas (wiping gas) of smearing of nozzle ejection.
Implemented the steel band of fused zinc, after pulling out from coating bath, be admitted in the alloying furnace of steam stove, induction heater etc. and heat.By this heating, the metal diffusing between coating and blank steel band is carried out alloying, and coating becomes zinc-iron alloy.This Heating temperature (alloying temperature) is preferably more than 500 ℃.If the alloying temperature is low than 500 ℃, then alloying speed is slow, so owing to the reduction of plate wire speed hinders productivity, perhaps needs to make the reply on the equipment of alloying furnace prolongation etc.The alloying temperature is high more, and alloying speed is fast more, if but the alloying temperature compares Ac 1Point is high, then makes the steel band high strength for the reason identical with maximum heating temperature with the upper limit of annealing temperature.The preferable range of alloying temperature is 550~650 ℃.
In order to carry out the adjustment of surfaceness, also can be for as above carrying out skin-pass with steel plate by the hot-pressed of various manufacture method manufacturings.Hot-pressed also can be other plated steel sheet with steel plate, and for example aluminium such as 55%Al-Zn alloy plated steel sheet is that plated steel sheet is also passable.
Embodiment
Following embodiment is that illustration is invented, and the intent of the present invention without limits.
With cold-rolled steel sheet (thickness of slab: 1.6mm) be the blank steel plate with the chemical constitution shown in the table 1.These steel plates are that slab with melting in the laboratory is by hot rolling and the cold rolling steel plate of making.
In addition, use the plating simulator, the steel plate of steel grade No.1 is implemented plating Al, and (the plating adhesion amount of each single face is 120g/m 2), the steel plate of No.2 is implemented molten zinc plating, and (the plating adhesion amount of each single face is 60g/m 2).Steel plate to No.2 carries out alloying thermal treatment (the Fe content in the plating epithelium is 15 quality %) again.The annealing temperature of plating simulator is 800 ℃, is 5 ℃/second from 800 ℃ of average cooling rates of ordering to Ms.
These steel plates are cut into the size of 1.6t * 100w * 200L (mm), in the process furnace of air atmosphere, heat, use dull and stereotyped steel metal die to carry out hot-pressed the steel plate after taking out by process furnace with the condition of table 2.The so-called hold-time reaches Ac from steel billet temperature after being meant in the stove of packing into 3Point is up to the time of taking out from stove.On steel plate, mount thermopair, carry out speed of cooling and measure.
For the hot-pressed steel plate member that obtains, for old austenite particle size determination, the tension test (JIS5 test film) carried out according to the method for section.
In addition, stacked from 6 pieces on the steel billet of hot-pressed steel plate member cutting thick 1.6mm down and carry out making V nick-break test sheet after screw connects, the pendulum impact test under-120 ℃ of the confessions.The impact value of toughness under-120 ℃ is 30J/cm 2Be zero (qualified) when above, be lower than 30J/cm 2The time be * (defective) that it shows with impact value.
The Ac of each steel plate 3Point, Ms point and upper critical cooling rate are measured by following method.
From the hot-rolled steel sheet cutting cylinder test film (Fig. 1) of diameter 3.0mm, long 10mm down, in atmosphere,, after 5 minutes, be cooled to room temperature with various speed of cooling in this temperature maintenance with 10 ℃/second heat-up rate heat test sheet to 900 ℃.By measure at this moment heating, the thermal expansion of test film in the cooling changes, and measures Ac 3Point, Ms point.In addition, the Vickers' hardness of the test film that obtains measure (load 49N, measure number: 3) and structure observation, according to the upper critical cooling rate of these resulting estimate steel plates.
These results are presented in the table 3.
[table 1]
[table 2]
[table 3]
In No.1~12 as example, hot-pressed steel plate member, old austenite particle diameter is fine to 10 μ m, and tensile strength is more than the 1.8GPa, and toughness value is also good.On the other hand, No.13 as a comparative example~15, old austenite particle diameter surpasses 10 μ m, and toughness value is not good.Among the comparative example, No.13 and 14 is that the chemical constitution of steel departs from the scope of the present invention outer example, though the chemical constitution of No.15 steel is in the scope of the present invention, but the Ms from hot-pressed o'clock to 150 ℃ average cooling rate is at extraneous example of the present invention.
When observing the micro organization of steel of steel plate member of hot extrusion with transmission electron microscope (TEM), the steel plate member of No.1~No.14 is confirmed to be the tissue that contains automatic tempered martensite.On the other hand, the steel plate member of No.15 is martensitic stucture fully.Even hot-pressed steel plate member has the tissue that contains automatic tempered martensite,, then still can not get good toughness if old austenite particle diameter surpasses 10 μ m.
Demonstration is as the TEM photo under the different multiplying of the hot-pressed steel plate member of the No.2 of example among Fig. 2.Epimere is 10000 times, and hypomere is 40000 times.The more than half of tissue is martensite, but in the big part of lath width, has fine needle-like cementite to separate out in this lath inside, and become automatic tempered martensite, and this can be obtained by 40000 times photo of hypomere confirming especially.For example, place indicated by the arrow is fine cementite among the figure.
In addition, for the alloy galvanized steel plate of steel grade No.2, use the blank of 1.0t * 80w * 320L (mm) size, after in the process furnace of air atmosphere, arriving 900 ℃, kept 1 minute in this temperature, take out, carry out the hot-pressed of shape for hat immediately by process furnace.Fig. 3 is the explanatory view of the medelling of cap moulding method.Hot-pressed condition is forming height 70mm, Rd (mould shoulder R) 8mm, Rp (drift shoulder R) 8mm, gap 1.0mm, folding pressure (fold pressure) 12.7kN.
Carry out low temperature impact test for this cap molding.After member being cooled to-40 ℃, make the hammer body of heavy 2450N (250kgf) collide member by height 1000mm, investigation has flawless.Consequently do not have crackle to take place, distinguish to have sufficient toughness.

Claims (17)

1. hot-pressed steel plate member, wherein, has following chemical constitution: C:0.26~0.45% in quality % in fact, Mn+Cr:0.5~3.0%, Nb:0.02~1.0%, satisfy the Ti of the amount of following formula (1), Si:0~0.5%, Ni:0~2%, Cu:0~1%, V:0~1%, Al:0~1%, B:0~0.01%, Mo:0~1.0%, Ca:0~0.005% and surplus: Fe and impurity, and, it is following and contain the micro organization of automatic tempered martensite to have old austenite median size and be 10 μ m, and tensile strength is more than the 1.8GPa
3.42N+0.001≤Ti≤3.42N+0.5…(1)
Ti in the formula and N represent the mass percentage content of this element in the steel, and N contains as impurity in steel.
2. hot-pressed steel plate member according to claim 1, wherein, described chemical constitution in quality % contain from Si:0.01~0.5%, Ni:0.01~2%, Cu:0.01~1%, V:0.01~1%, Al:0.01~1%, B:0.001~0.01%, Mo:0.01~1.0% and Ca:0.001~0.005%, select more than a kind or 2 kinds.
3. hot-pressed steel plate member according to claim 1 and 2, wherein, the amount more than a kind or 2 kinds of the P that contains as impurity in the described chemical constitution, S and N satisfies below the P:0.005%, reaches below the N:0.002% below the S:0.005% in quality %.
4. hot-pressed steel plate of using, it can make following hot-pressed steel plate member: this hot-pressed steel plate member has following chemical constitution: C:0.26~0.45% in quality % in fact, Mn+Cr:0.5~3.0%, Nb:0.02~1.0%, satisfy the Ti of the amount of following formula (1), Si:0~0.5%, Ni:0~2%, Cu:0~1%, V:0~1%, Al:0~1%, B:0~0.01%, Mo:0~1.0%, Ca:0~0.005%, and surplus: Fe and impurity, this hot-pressed steel plate member is by hot-pressed, tensile strength is more than the 1.8GPa
3.42N+0.001≤Ti≤3.42N+0.5…(1)
Ti in the formula and N are the meanings of the mass percentage content of this element in the steel, and N contains as impurity in steel.
5. the hot-pressed steel plate of using according to claim 4, wherein, described chemical constitution in quality % contain from Si:0.01~0.5%, Ni:0.01~2%, Cu:0.01~1%, V:0.01~1%, Al:0.01~1%, B:0.001~0.01%, Mo:0.01~1.0% and Ca:0.001~0.005%, select more than a kind or 2 kinds.
6. according to claim 4 or the 5 described hot-pressed steel plates of using, wherein, the amount more than a kind or 2 kinds of the P that contains as impurity in the described chemical constitution, S and N satisfies below the P:0.005%, reaches below the N:0.002% below the S:0.005% in quality %.
7. the manufacture method of a hot-pressed steel plate member, wherein, comprise following operation: the steel plate that will have following chemical constitution is at Ac 3Above (the Ac of point 3Point+100 ℃) after following temperature field keeps time below 5 minutes, implement hot-pressed to this steel plate, make that to reach the speed of cooling that Ms orders be more than the upper critical cooling rate, and the average cooling rate that makes Ms o'clock to 150 ℃ is 10~500 ℃/second, so hot-pressed pyritous steel plate is cooled off, described steel plate contains C:0.26~0.45% in quality % in fact, Mn+Cr:0.5~3.0%, Nb:0.02~1.0%, satisfy the Ti of the amount of following formula (1), Si:0~0.5%, Ni:0~2%, Cu:0~1%, V:0~1%, Al:0~1%, B:0~0.01%, Mo:0~1.0%, Ca:0~0.005% and surplus: Fe and impurity
3.42N+0.001≤Ti≤3.42N+0.5…(1)
Ti in the formula and N are the meanings of the mass percentage content of this element in the steel, and N contains as impurity in steel.
8. the manufacture method of a hot-pressed steel plate member wherein, comprises following operation: to steel plate with following chemical constitution than Ac 3The temperature that point is low uses metal die to carry out extrusion molding, the steel plate of extrusion molding is put into the state of this metal die, at Ac 3Above (the Ac of point 3Point+100 ℃) following temperature field keeps the time below 5 minutes, make then that to reach speed of cooling that Ms orders be that upper critical cooling rate is above and make Ms o'clock to 150 ℃ average cooling rate be 10~500 ℃/second to cool off, this steel plate contains C:0.26~0.45% in quality % in fact, Mn+Cr:0.5~3.0%, Nb:0.02~1.0%, satisfy the Ti of the amount of following formula (1), Si:0~0.5%, Ni:0~2%, Cu:0~1%, V:0~1%, Al:0~1%, B:0~0.01%, Mo:0~1.0%, Ca:0~0.005% and surplus: Fe and impurity
3.42N+0.001≤Ti≤3.42N+0.5…(1)
Ti in the formula and N are the meanings of the mass percentage content of this element in the steel, and N contains as impurity in steel.
9. hot-pressed manufacture method with steel plate, wherein, comprise following operation: will have the steel ingot of following chemical constitution or steel billet 1050~1300 ℃ temperature in hot rolling, finish this hot rolling 800~950 ℃ temperature, batch the steel band that obtains by hot rolling 500~700 ℃ temperature, this steel ingot or steel billet contain C:0.26~0.45% in quality % in fact, Mn+Cr:0.5~3.0%, Nb:0.02~1.0%, satisfy the Ti of the amount of following formula (1), Si:0~0.5%, Ni:0~2%, Cu:0~1%, V:0~1%, Al:0~1%, B:0~0.01%, Mo:0~1.0%, Ca:0~0.005% and surplus: Fe and impurity
3.42N+0.001≤Ti≤3.42N+0.5…(1)
Ti in the formula and N are the meanings of the mass percentage content of this element in the steel, and N contains as impurity in steel.
10. method according to claim 9 wherein, also comprises the steel band that expansion is batched, and this steel band is implemented de-scaling handle and cold rolling operation.
11. method according to claim 10 wherein, also comprises cold rolling steel band at (Ac 1Point+10 ℃) above Ac 3After the following temperature field of point kept for 10 seconds above, be cooled to 300~500 ℃ temperature field with 1~100 ℃/second average cooling rate, then with this steel band after 300~500 ℃ temperature field keeps 30 second~10 minute, be cooled to the operation of room temperature with 1~50 ℃/second average cooling rate.
12. method according to claim 10 wherein, also comprises cold rolling steel band at (Ac 1Point-100 ℃) above (Ac 1Point+30 ℃) following temperature field keeps being cooled to the operation of room temperature with 1~100 ℃/hour average cooling rate after 1~24 hour.
13. method according to claim 9 wherein, also comprises the steel band that expansion is batched, and this steel band is implemented desquamation processing and molten zinc plating, then at Ac more than 500 ℃ 1The following temperature field of point is implemented the heat treated operation of alloying to this steel band.
14. method according to claim 10, wherein, also comprise cold rolling steel band after 700~900 ℃ temperature field is implemented annealing, be cooled to temperature field below 500 ℃ with 1~60 ℃/second average cooling rate, this steel band is implemented molten zinc plating, thereafter at Ac more than 500 ℃ 1The following temperature field of point is implemented the heat treated operation of alloying.
15. method according to claim 12 wherein, comprises the steel band that is cooled to room temperature is implemented molten zinc plating, thereafter at Ac more than 500 ℃ 1The following temperature field of point is implemented the heat treated operation of alloying.
16. according to each described method in the claim 7~15, wherein, described chemical constitution in quality % contain from Si:0.01~0.5%, Ni:0.01~2%, Cu:0.01~1%, V:0.01~1%, Al:0.01~1%, B:0.001~0.01%, Mo:0.01~1.0% and Ca:0.001~0.005%, select more than a kind or 2 kinds.
17. according to each described method in the claim 7~16, wherein, the amount more than a kind or 2 kinds of the P that contains as impurity in the described chemical constitution, S and N satisfies below the P:0.005%, reaches below the N:0.002% below the S:0.005% in quality %.
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Family Cites Families (12)

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JP4306411B2 (en) * 2003-10-31 2009-08-05 住友金属工業株式会社 Steel plate for heat treatment and its manufacturing method
JP4673558B2 (en) * 2004-01-26 2011-04-20 新日本製鐵株式会社 Hot press molding method and automotive member excellent in productivity
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