EP2171102B1 - Metallstreifen mit veränderlicher dicke in längsrichtung - Google Patents

Metallstreifen mit veränderlicher dicke in längsrichtung Download PDF

Info

Publication number
EP2171102B1
EP2171102B1 EP08718031.1A EP08718031A EP2171102B1 EP 2171102 B1 EP2171102 B1 EP 2171102B1 EP 08718031 A EP08718031 A EP 08718031A EP 2171102 B1 EP2171102 B1 EP 2171102B1
Authority
EP
European Patent Office
Prior art keywords
strip
steel
mpa
sections
yield strength
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Active
Application number
EP08718031.1A
Other languages
English (en)
French (fr)
Other versions
EP2171102A2 (de
Inventor
Hai Wu
Camile Wilbert José HOL
Pieter Jacob Van Popta
Willem Cornelis Verloop
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Muhr und Bender KG
Original Assignee
Muhr und Bender KG
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Muhr und Bender KG filed Critical Muhr und Bender KG
Priority to EP08718031.1A priority Critical patent/EP2171102B1/de
Priority to PL08718031T priority patent/PL2171102T3/pl
Publication of EP2171102A2 publication Critical patent/EP2171102A2/de
Application granted granted Critical
Publication of EP2171102B1 publication Critical patent/EP2171102B1/de
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12201—Width or thickness variation or marginal cuts repeating longitudinally

Definitions

  • the invention relates to a strip of steel having a variable thickness in its length direction with at least thicker and thinner sections, the strip having been cold rolled to form the thicker and thinner sections, one thicker and one thinner section having a length of at most a few metres. as defined by the corresponding claims.
  • a strip of steel having a variable thickness in its length direction is often made such that the strip has a repetitive thickness variation, wherein a thicker section of the strip is followed by a thinner section which is thereafter followed by a thicker section, and this is repeated over the length of the strip.
  • the thinner sections all have approximately the same length, and so have the thicker sections.
  • One thicker and one thinner section have a length of at most a few metres.
  • One strip can have at least a few hundred thicker and thinner sections.
  • the thicker and thinner sections have a thickness between a few tenths of a millimetre and a few millimetres.
  • the strip is rolled into three or more different thicknesses which repeat along the length of the strip. Due to the fact that the strip of steel has been cold rolled, between the thicker and thinner sections a transitional section will be formed in which the thickness of the strip gradually changes from the thickness of one section to the thickness of the following section.
  • the length of this transitional section is determined by the thickness change between the sections, the rolling speed and the speed with which the cold rolling mill can change the distance between the rolls, to mention the most important parameters.
  • the length of the transitional section is of the same order as the length of the thicker and thinner sections or even shorter.
  • the width of the strip can be from a few decimetre up to about two meter.
  • the strip can be slit into two or more strips having a reduced width, but this is not always required.
  • Such a strip is cut into pieces which are called tailor rolled blanks (TRBs), for instance for the automotive industry.
  • TRBs tailor rolled blanks
  • the blanks thus have at least two different thicknesses over their lengths, as required for the purpose and place they are used in.
  • the thickness is considerably reduced in the thinner portions. This results in a hardening of the steel, such that the rolled strip cannot be used directly.
  • the steel strip has to be annealed to release the stresses in the strip and/or to recrystallise the strip.
  • Annealing of a steel strip without thickness variations can be performed either by batch annealing or by continuous annealing.
  • Annealing of steel strip having a variable thickness in its length direction is performed only by batch annealing, so as to provide the same temperature to both the thinner and the thicker sections.
  • Batch annealing though is more expensive than continuous annealing, and it usually has a somewhat deteriorating effect on the strength of the steel. Due to the slow heating and cooling rate experienced in the case of batch annealing it is not attractive for all steel types, especially for steel types having a higher strength.
  • At least one of these objects is reached using a strip of steel having a variable thickness in its length direction with at least thicker sections and thinner sections, the strip having been cold rolled to form the thicker and thinner sections, one thicker and one thinner section having a length of at most a few meter, which strip has been annealed, wherein the annealing is performed by continuous annealing.
  • the inventors of the present invention have observed that, contrary to the well-known batch annealing which is the only method of annealing used for strip having a variable thickness according to the state of the art, it is nevertheless possible to continuous anneal a strip of steel having a variable thickness in length direction.
  • Continuous annealing has the advantage that it is a faster process and provides new and better tailor rolled blanks. Tailor rolled blanks produced using continuous annealing have better mechanical properties than tailor rolled blanks produced using batch annealing having the same composition and rolling history, such as a higher mechanical strength, and so have the strips of steel from which such tailor rolled blanks are produced.
  • a strip having a variable thickness will have different mechanical properties in the different sections because of the variation in cold rolling reduction, whereas the annealing temperature and heating rate will be the same in all sections.
  • a higher cold rolling reduction will produce different mechanical properties, for instance a higher yield strength.
  • the advantage of continuous annealing over batch annealing is that with continuous annealing the sections with a variable thickness will also experience different temperatures and heating rates. In a thinner section the temperature will reach higher values than in a thicker section. The higher annealing temperature experienced in the thinner sections will reduce the strength, which partly or completely compensates the effect of the higher cold rolling reduction.
  • the yield strength of the thicker sections is equal to or higher than the yield strength of the thinner sections. This is advantageous because the TRBs made from such strips are used for parts that need to have more strength in the thicker section than in the thinner section.
  • the steel strip is a DP, TRIP or multi phase high strength steel.
  • These high strength steels can not be produced using batch annealing, so continuous annealing makes the use of DP, TRIP and multi phase high strength steels possible for producing strip having a variable thickness and the TRBs made thereof.
  • the steel strip is a HSLA steel or a low carbon steel.
  • Using continuous annealing for these steel types provides strip having a variable thickness and TRBs made thereof that have better mechanical properties, such as a higher yield strength.
  • the strip of steel is a HSLA steel or low carbon steel
  • the thinner sections are recrystallised and the difference in yield strength of the thicker and thinner sections is smaller than in the same HSLA or low carbon steel strip that has been batch annealed.
  • the recrystallised thinner sections reach a higher temperature due to the continuous annealing, compared to batch annealing, and therefore the thinner sections have for instance a higher yield strength.
  • the yield strengths of the thicker and thinner sections have values that are more near to each other than the corresponding values of batch annealed strip having the same composition.
  • the composition of the steel has lower values of alloying elements than in a batch annealed HSLA or low carbon steel having the same yield strength of the thinner sections. Since the yield strength is better for continuous annealed strip having a variable thickness then for batch annealed strip with the same composition, it is possible to provide strip having a variable thickness with the same yield strength as batch annealed strip, using a continuous annealed strip having lower values of alloying elements (which strip, when batch annealed, would have a lower yield strength). Thus, the steel strip having a variable thickness is cheaper.
  • the steel has the following composition in wt%: C 0.03 to 0.08 Mn 0.1 to 1.2 Si ⁇ 1.0 P ⁇ 0.1 Nb ⁇ 0.07 V ⁇ 0.5 Ti ⁇ 0.1 the remainder being iron and inevitable impurities.
  • This is a normal composition for a low carbon steel, wherein the steel can contain one or more of the optional alloying elements Si, P, Nb, V and Ti.
  • Such a steel composition for continuous annealed strips for vehicle bodies is disclosed in EP-A 1 571 229 .
  • the steel contains C, Mn, and optionally Si, P, Nb, V, and Ti, the remainder being iron and inevitable impurities, and is characterised by the equation: YS ⁇ 250 + 255 Mn / 6 + Si / 24 + 716 P + 2938 Nb + 600 V + 2000 Ti MPa with Mn, Si, P, Nb, V, Ti in wt% and YS being the yield strength in the thinner sections of the strip.
  • This equation shows that by using continuous annealing a high yield strength can be achieved in the thinner sections of the strip with less alloying elements than would be needed when such a strip had been batch annealed.
  • the steel is characterised by the equation YS ⁇ 270 + 225(Mn/6 + Si/24) + 716P + 2938Nb + 600V + 2000Ti [MPa]. Due to optimised process conditions for the continuous annealing, the steel strip having a variable thickness will reach the higher yield strength according to this equation.
  • the strip of steel is characterised by the equation A 80 ⁇ ⁇ 0.05 * YS + 40 with A80 being the total elongation in the thinner sections of the strip and YS being the yield strength in the thinner sections of the strip.
  • A80 being the total elongation in the thinner sections of the strip
  • YS being the yield strength in the thinner sections of the strip.
  • the steel in the thinner sections has a tensile strength above 600 MPa and a yield strength below 400 MPa.
  • the steel of this strip is for instance a dual phase steel that has been temper rolled.
  • the steel in the thinner sections has a tensile strength above 600 MPa and a yield strength below 300 MPa.
  • the lower yield strength is reached by an optimised rolling schedule before and/or after the continuous annealing of the strip.
  • the steel in the thinner sections has a tensile strength above 800 MPa and a yield strength below 550 MPa.
  • the steel of this strip can be a dual phase steel as well, having a composition with higher amounts of alloying elements, which has been temper rolled.
  • the steel in the thinner sections has a tensile strength above 800 MPa and a yield strength below 450 MPa.
  • the lower yield strength is reached by an optimised rolling schedule before and/or after the continuous annealing of the strip.
  • the steel in the thinner sections has a tensile strength above 980 MPa and a yield strength below 750 MPa.
  • the steel can be a dual phase steel, having a composition having still higher amounts of alloying elements, which has been temper rolled.
  • the steel in the thinner sections has a tensile strength above 980 MPa and a yield strength below 650 MPa. Again, the lower yield strength is reached by an optimised rolling schedule before and/or after the continuous annealing of the strip.
  • a tailor rolled blank produced from a strip of steel according to the description above.
  • the tailor rolled blanks are cut from the strip having a variable thickness, and these tailor rolled blanks are used in the automotive industry, for instance.
  • the temperature T is presented along the vertical axis and time t along the horizontal axis.
  • FIG 1 a typical continuous annealing time-temperature curve is presented.
  • the process in a continuous annealing line for steel strip often consists of a sequential of different heating and cooling sections.
  • a fast heating section H1
  • a slow heating section H2
  • This maximum temperature is normally higher than the recrystallisation temperature to ensure complete recrystallisation of the microstructure of the steel.
  • the maximum temperature must be higher than 720 °C to bring the material in the two-phase region of austenite and ferrite.
  • FIG. 2 the effect of continuous annealing on TRB is illustrated.
  • the sections with variation in thickness will show a difference in heating and cooling rates, and as a result will follow different time-temperature cycles.
  • the line S1 indicates the time-temperature cycle for the thinner sections of the TRB
  • the line S2 indicates the time-temperature cycle for the thicker sections of the TRB.
  • the exact time-temperature profile depends on many parameters, such as the thickness profile of the strip, line speed, width of the strip, heating and cooling capacity of individual sections in the continuous annealing line.
  • Noteworthy in figure 2 is the relatively large difference in temperature at the end of the fast heating section ( ⁇ T1).
  • the difference ⁇ T1 can in some cases reach values of more than 100 °C.
  • the difference in temperature at maximum temperature is a critical parameter for successfully producing continuous annealed TRB. If ⁇ T2 becomes too big the mechanical properties of the thicker and/or thinner sections become unstable. If the temperature of the thicker sections becomes too low than the material is not fully recrystallised and the mechanical properties, especially the elongation, are not fully developed and extremely sensitive to small fluctuations of the maximum temperature. On the other hand, if the temperature of the thinner sections becomes too high, higher than 800 °C, the mechanical properties of especially high strength steels will deteriorate. The deterioration is caused by the fact that the grain size will increase with the maximum temperature, because the fine grain size after cold rolling and recrystallisation will be eliminated by transformation.
  • the difference in temperature between the thicker en thinner sections of the TRB during cooling ( ⁇ T3 or ⁇ T4) is also of importance. Especially if a metal coating process like hot dip galvanising is applied.
  • a metal coating process like hot dip galvanising is applied.
  • the zinc will not make good contact with the strip surface and problems with zinc adherence and surface quality will arise.
  • the zinc only starts to solidify below a temperature of 420 °C.
  • the temperature of the strip entering the zinc bath is too high, the amount of iron dissolving in the zinc increases and thus the amount of metallic dross formation in the zinc bath. This can lead to a bad surface quality of the material.
  • a high strip temperature can cause increased alloying between the zinc layer and the substrate.
  • the temperature differences between the thick en thin sections of the TRB can be reduced by selective heating. This is illustrated in figure 3 . At some point during heating of the strip the temperature of the thicker sections is increased (H3). The temperature of the thicker sections can be increased to a temperature level reaching that of the thin section, or even above. In this way the difference in maximum temperature ( ⁇ T2) can be reduced significantly.
  • a steel strip is formed by hot rolling. After hot rolling, a steel strip having a variable thickness in length direction is formed by cold rolling both the thicker sections and the thinner sections with a reduction of at least 15%. As a result, both the thicker and the thinner sections will recrystallise during annealing.
  • a steel strip is formed by hot rolling. After hot rolling, a steel strip having a variable thickness in length direction is formed by cold rolling the thicker sections with a reduction of less than 15%, usually approximately 5%, and by cold rolling the thinner sections with a reduction of at least 15%, usually between 20 and 50%.
  • This rolling type has the advantage that in the thicker sections the hot rolled yield strength is increased by a small cold rolling reduction, which improves the yield strength, which is to a large extend retained during subsequent annealing. Another advantage is that cold rolling of the thinner sections is more easy because only the thinner sections have to be reduced.
  • the yield strength of the continuous annealed strip in the thinner sections is 73 MPa higher than for the batch annealed product. Also the yield strength in the thicker sections is higher after continuous annealing.
  • Producing TRB by only applying a large reduction to the thinner sections is a production route that has many economical advantages. In case of batch annealing the inhomogeneity of the mechanical properties between the thinner en thicker sections is a problem.
  • the advantage of a high yield strength in the thicker sections, based on the mechanical properties in hot rolled condition, can not be utilised fully in case of batch annealing because the yield strength in the thinner sections will always be much lower.
  • Line speed in a continuous annealing line is important economical parameter. If line speed is low than cooling devices like gas jet cooling have to be operated at minimum capacity, outside the normal operation modus, making it more difficult to control the strip temperature before hot dip galvanising. Producing TRB with a normal line speed is both for economical and practical reasons beneficial. Selective heating is an effective method to enable the producer to increase line speed and at the same time improve the mechanical properties of the TRB.
  • a dual phase steel is presented.
  • Essential for producing dual phase kind of steel types is a high annealing temperature (in two phase region) and relatively high cooling rate to promote transformation from austenite to martensite, bainite and/or retained austenite.
  • a low line speed is a disadvantage because also the cooling rate will be slow.
  • Figure 4 shows a comparison between the batch annealing and the continuous annealing for a number of low carbon steel types, of which the composition is given in table 3.
  • the Yield Strength (YS) in the sections that are significantly reduced by cold rolling is given on the vertical axis, on the horizontal axis the different steel types are indicated.
  • Such steel types are normal steel types that are produced and on the market. From Figure 4 it is clear that the yield strength of continuous annealed steel is significantly higher than the yield strength of the same steel types that are batch annealed.
  • Such improved yield strengths are also reached in the thinner sections of a strip of steel having a variable thickness when it is continuous annealed instead of batch annealed, as elucidated in the examples above.
  • Table 3 Typical composition (in wt%) of different steel types Steel type C Mn Si P Nb V LC 0.045 0.22 ⁇ 0.01 ⁇ 0.01 ⁇ 0.002 ⁇ 0.002 Nb1 0.045 0.25 ⁇ 0.01 ⁇ 0.01 0.009 ⁇ 0.002 Nb2 0.06 0.25 ⁇ 0.01 ⁇ 0.01 0.017 ⁇ 0.002 P 0.06 0.5 ⁇ 0.01 0.085 ⁇ 0.002 ⁇ 0.002 V 0.045 0.8 ⁇ 0.01 ⁇ 0.01 0.013 0.04 Nb3 0.07 0.5 ⁇ 0.01 ⁇ 0.01 0.026 ⁇ 0.002 Nb4 0.075 1 0.3 ⁇ 0.01 0.03 ⁇ 0.002

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Metal Rolling (AREA)

Claims (12)

  1. Stahlband mit variabler Dicke in Längsrichtung mit mindestens dickeren Abschnitten und dünneren Abschnitten mit einem Übergangsabschnitt dazwischen, so dass das Band eine sich wiederholende Dickenvariation aufweist, wobei das Band kaltgewalzt worden ist, um die dickeren und dünneren Abschnitte zu bilden, wobei ein dickerer und ein dünnerer Abschnitt eine Länge von höchstens ein paar Metern aufweist, wobei das Band geglüht wurde, wobei das Band in Stücke zu schneiden ist, die maßgewalzte Platinen ("tailor rolled blanks") genannt werden, dadurch gekennzeichnet, dass der Stahl die folgende Zusammensetzung in Gew.-% aufweist: C 0,03 bis 0,08 Mn 0,1 bis 1,2 Si ≤ 1.0 P ≤ 0,1 Nb ≤ 0,07 V ≤ 0,5 Ti ≤ 0,1
    wobei der Rest Eisen und unvermeidliche Verunreinigungen ist, wobei das Glühen durch kontinuierliches Glühen erfolgt ist und wobei gilt YS ≥ 250 + 225 Mn / 6 + Si / 24 + 716 P + 2938 Nb + 600 V + 2000 Ti MPa ,
    Figure imgb0006
     mit Mn, Si, P, Nb, V, Ti in Gew.-% und wobei YS die Streckgrenze in den dünneren Abschnitten des Streifens ist.
  2. Stahlband nach Anspruch 1, wobei die Streckgrenze der dickeren Abschnitte gleich oder höher als die Streckgrenze der dünneren Abschnitte ist.
  3. Stahlband nach Anspruch 1 oder 2, wobei nur die dünneren Abschnitte rekristallisiert sind und wobei der Unterschied in der Streckgrenze der dickeren und dünneren Abschnitte kleiner ist als im gleichen HSLA-oder kohlenstoffarmen Stahlband, der in Chargen geglüht wurde.
  4. Stahlband nach einem oder mehreren der Ansprüche 1 bis 3, wobei gilt YS ≥ 270 + 225 Mn / 6 + Si / 24 + 716 P + 2938 Nb + 600 V + 2000 Ti MPa .
    Figure imgb0007
  5. Stahlband nach einem der Ansprüche 1 bis 4, wobei gilt A 80 ≥ − 0 , 05 * YS + 40
    Figure imgb0008
     wobei A80 die Gesamtdehnung in den dünneren Abschnitten des Bands ist und YS die Streckgrenze in den dünneren Abschnitten des Bands ist.
  6. Stahlband nach Anspruch 1, wobei der Stahl in den dünneren Abschnitten eine Zugfestigkeit über 600 MPa und eine Streckgrenze unter 400 MPa aufweist.
  7. Stahlband nach Anspruch 6, wobei der Stahl in den dünneren Abschnitten eine Zugfestigkeit über 600 MPa und eine Streckgrenze unter 300 MPa aufweist.
  8. Stahlband nach Anspruch 1, wobei der Stahl in den dünneren Abschnitten eine Zugfestigkeit über 800 MPa und eine Streckgrenze unter 550 MPa aufweist.
  9. Stahlband nach Anspruch 8, wobei der Stahl in den dünneren Abschnitten eine Zugfestigkeit über 800 MPa und eine Streckgrenze unter 450 MPa aufweist,
  10. Stahlband nach Anspruch 1, wobei der Stahl in den dünneren Abschnitten eine Zugfestigkeit über 980 MPa und eine Streckgrenze unter 750 MPa aufweist.
  11. Stahlband nach Anspruch 10, wobei der Stahl in den dünneren Abschnitten eine Zugfestigkeit über 980 MPa und eine Streckgrenze unter 650 MPa aufweist.
  12. Maßgewalzte Platine ("tailor rolled blank"), die aus einem Stahlband nach einem der vorherigen Ansprüche hergestellt ist.
EP08718031.1A 2007-07-19 2008-03-19 Metallstreifen mit veränderlicher dicke in längsrichtung Active EP2171102B1 (de)

Priority Applications (2)

Application Number Priority Date Filing Date Title
EP08718031.1A EP2171102B1 (de) 2007-07-19 2008-03-19 Metallstreifen mit veränderlicher dicke in längsrichtung
PL08718031T PL2171102T3 (pl) 2007-07-19 2008-03-19 Pas stali o zmiennej grubości w kierunku długości

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
EP07014186 2007-07-19
EP08718031.1A EP2171102B1 (de) 2007-07-19 2008-03-19 Metallstreifen mit veränderlicher dicke in längsrichtung
PCT/EP2008/053310 WO2008068352A2 (en) 2007-07-19 2008-03-19 A strip of steel having a variable thickness in length direction

Publications (2)

Publication Number Publication Date
EP2171102A2 EP2171102A2 (de) 2010-04-07
EP2171102B1 true EP2171102B1 (de) 2017-09-13

Family

ID=38596069

Family Applications (1)

Application Number Title Priority Date Filing Date
EP08718031.1A Active EP2171102B1 (de) 2007-07-19 2008-03-19 Metallstreifen mit veränderlicher dicke in längsrichtung

Country Status (7)

Country Link
US (1) US20100304174A1 (de)
EP (1) EP2171102B1 (de)
JP (1) JP5425770B2 (de)
CN (1) CN101802230B (de)
HU (1) HUE037337T2 (de)
PL (1) PL2171102T3 (de)
WO (1) WO2008068352A2 (de)

Families Citing this family (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2008102012A1 (en) 2007-02-23 2008-08-28 Corus Staal Bv Method of thermomechanical shaping a final product with very high strength and a product produced thereby
CN101755063A (zh) * 2007-07-19 2010-06-23 科鲁斯斯塔尔有限公司 用于对在长度方向具有不同厚度的钢带进行退火的方法
EP2025771A1 (de) * 2007-08-15 2009-02-18 Corus Staal BV Verfahren zur Herstellung eines beschichteten Stahlbandes zur Herstellung von Platinenzuschnitten zur thermomechanischen Formgebung, so hergestelltes Band und Verwendung eines solchen Bandes
DE102008038865A1 (de) * 2008-08-08 2010-02-11 Sms Siemag Aktiengesellschaft Verfahren zur Herstellung von Halbzeug, insbesondere Stahlband, mit Dualphasengefüge
CN102397875B (zh) * 2010-09-16 2014-01-01 鞍钢股份有限公司 一种纵向变厚度钢板的生产方法
CN104338748B (zh) * 2013-07-24 2016-04-27 宝山钢铁股份有限公司 一种用于变厚度带材轧制的两道次轧制方法
CN104561517B (zh) * 2013-10-18 2016-08-17 沈阳东宝海星金属材料科技有限公司 板带材周期变温度差异化退火方法和装置
BR112016016487B1 (pt) * 2014-01-17 2021-03-02 Aperam processos de fabricação, tira de espessura variável, produto semiacabado, segmento de tubo e conjunto
JP6369537B2 (ja) 2014-04-23 2018-08-08 新日鐵住金株式会社 テーラードロールドブランク用熱延鋼板、テーラードロールドブランク、及びそれらの製造方法
EP3118343B1 (de) * 2015-07-14 2017-11-22 Borcelik Celik San. ve Tic. A.S. Schränke für haushaltsgeräte mit hoher dauerhaftigkeit und reduzierter dicke
EP3301197B1 (de) * 2016-09-29 2021-10-27 Outokumpu Oyj Verfahren zur kaltverformung eines austenitischen stahls
US20200003937A1 (en) 2018-06-29 2020-01-02 Applied Materials, Inc. Using flowable cvd to gap fill micro/nano structures for optical components
CN115816932B (zh) * 2022-11-30 2024-04-19 安徽工业大学 一种高强度蜂窝板的结构设计及制备工艺

Family Cites Families (33)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5924166B2 (ja) * 1977-10-20 1984-06-07 新日本製鐵株式会社 ストリツプの連続加熱に於ける板温制御方法
SU863681A1 (ru) * 1979-04-09 1981-09-15 Предприятие П/Я В-2996 Способ управлени отжигом полосы в многозонной печи
JPS58120742A (ja) * 1982-01-11 1983-07-18 Nippon Steel Corp 鋼帯の冷却制御方法
JPS60169525A (ja) * 1984-02-15 1985-09-03 Mitsubishi Heavy Ind Ltd 連続焼鈍炉冷却帯の鋼帯冷却方法
NL8800391A (nl) * 1988-02-17 1989-09-18 Hoogovens Groep Bv Verouderingsbestendig laaggelegeerd warmgewalst bandvormig vervormingsstaal.
JPH02258933A (ja) * 1989-03-29 1990-10-19 Sumitomo Metal Ind Ltd 連続焼鈍炉における板温制御方法
JPH06932B2 (ja) * 1989-04-20 1994-01-05 川崎製鉄株式会社 冷間圧延ステンレス鋼帯の連続焼鈍方法
JP2825535B2 (ja) * 1989-07-17 1998-11-18 川崎製鉄株式会社 連続焼鈍炉の炉内圧制御方法
JPH04103722A (ja) * 1990-08-24 1992-04-06 Kawasaki Steel Corp 冷間圧延ステンレス鋼帯の連続焼鈍方法
FR2688802B1 (fr) * 1992-03-19 1994-09-30 Stein Heurtey Procede de traitement thermique de bandes metalliques.
KR960010811B1 (ko) * 1992-04-16 1996-08-09 신니뽄세이데스 가부시끼가이샤 자성이 우수한 입자배향 전기 강 시트의 제조방법
CN2249134Y (zh) * 1996-04-23 1997-03-12 胡知龙 一种横向不等厚钢条
FR2780984B1 (fr) * 1998-07-09 2001-06-22 Lorraine Laminage Tole d'acier laminee a chaud et a froid revetue et comportant une tres haute resistance apres traitement thermique
EP1571229B1 (de) * 2000-02-29 2007-04-11 JFE Steel Corporation Hochfestes warmgewalztes Stahlblech mit ausgezeichneten Reckalterungseigenschaften
FR2807447B1 (fr) * 2000-04-07 2002-10-11 Usinor Procede de realisation d'une piece a tres hautes caracteristiques mecaniques, mise en forme par emboutissage, a partir d'une bande de tole d'acier laminee et notamment laminee a chaud et revetue
DE10055338C1 (de) * 2000-11-08 2002-03-07 Thyssenkrupp Stahl Ag Verfahren zum Herstellen eines bei niedrigen Verformungsgraden kaltverformten Kaltbandes
JP2002331317A (ja) * 2001-04-27 2002-11-19 Honda Motor Co Ltd 車体パネル用ブランク材
JP2003105500A (ja) * 2001-09-26 2003-04-09 Nippon Metal Ind Co Ltd ステンレス鋼／銅クラッドおよびその製造方法
DE10307184B3 (de) * 2003-02-20 2004-04-08 Benteler Automobiltechnik Gmbh Verfahren zur Herstellung eines gehärteten Strukturbauteils für den Fahrzeugbau
DE10315357B4 (de) * 2003-04-03 2005-05-25 Muhr Und Bender Kg Verfahren zum Walzen und Walzanlage zum Walzen von Metallband
JP2004315883A (ja) * 2003-04-15 2004-11-11 Nisshin Steel Co Ltd ブラウン管バンド用高強度高透磁率鋼板およびその製造法
ATE478971T1 (de) * 2003-07-29 2010-09-15 Voestalpine Stahl Gmbh Verfahren zum herstellen von geharteten bauteilen aus stahlblech
KR100884104B1 (ko) * 2004-01-14 2009-02-19 신닛뽄세이테쯔 카부시키카이샤 도금 밀착성 및 구멍 확장성이 우수한 용융 아연 도금 고강도 강판과 그 제조 방법
US20060130940A1 (en) * 2004-12-20 2006-06-22 Benteler Automotive Corporation Method for making structural automotive components and the like
DE102005025026B3 (de) * 2005-05-30 2006-10-19 Thyssenkrupp Steel Ag Verfahren zum Herstellen eines Metallbauteils mit aneinander angrenzenden Abschnitten unterschiedlicher Materialeigenschaften
US7543384B2 (en) * 2005-08-11 2009-06-09 Gm Global Technology Operations, Inc. Method of making a variable thickness member for a vehicle
EP1767659A1 (de) * 2005-09-21 2007-03-28 ARCELOR France Herstellungsverfahren eines Stahlwerkstücks mit mehrphasigem Mikrogefüge
CN1850375A (zh) * 2006-04-29 2006-10-25 东北大学 变厚度钢板的连续轧制方法
WO2008102012A1 (en) * 2007-02-23 2008-08-28 Corus Staal Bv Method of thermomechanical shaping a final product with very high strength and a product produced thereby
DE102007013739B3 (de) * 2007-03-22 2008-09-04 Voestalpine Stahl Gmbh Verfahren zum flexiblen Walzen von beschichteten Stahlbändern
US7743232B2 (en) * 2007-07-18 2010-06-22 Advanced Micro Devices, Inc. Multiple-core processor with hierarchical microcode store
CN101755063A (zh) * 2007-07-19 2010-06-23 科鲁斯斯塔尔有限公司 用于对在长度方向具有不同厚度的钢带进行退火的方法
EP2025771A1 (de) * 2007-08-15 2009-02-18 Corus Staal BV Verfahren zur Herstellung eines beschichteten Stahlbandes zur Herstellung von Platinenzuschnitten zur thermomechanischen Formgebung, so hergestelltes Band und Verwendung eines solchen Bandes

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
None *

Also Published As

Publication number Publication date
WO2008068352A3 (en) 2008-07-24
JP2010533787A (ja) 2010-10-28
JP5425770B2 (ja) 2014-02-26
EP2171102A2 (de) 2010-04-07
PL2171102T3 (pl) 2018-02-28
HUE037337T2 (hu) 2018-08-28
US20100304174A1 (en) 2010-12-02
CN101802230B (zh) 2012-10-17
CN101802230A (zh) 2010-08-11
WO2008068352A2 (en) 2008-06-12

Similar Documents

Publication Publication Date Title
EP2171102B1 (de) Metallstreifen mit veränderlicher dicke in längsrichtung
EP2171104B9 (de) Verfahren zum glühen eines stahlbands mit variabler dicke in längsrichtung
EP3396010B1 (de) Aluminium-eisen-legierungsbeschichtetes stahlblech zur heisspressformung mit hervorragender wasserstoffverzögerter bruchfestigkeit, hervorragendem schälwiderstand und hervorragender schweissbarkeit, warmformteil damit, sowie verfahren zur herstellung davon
EP2183402B1 (de) Verfahren zur herstellung eines beschichteten stahlbandes zur herstellung von platinenzuschnitten zur thermomechanischen formgebung, so hergestelltes band und verwendung eines solchen bandes
EP2546368B1 (de) Verfahren zur herstellung eines hochfesten stahlblechs
EP3653736B1 (de) Warmgewalztes stahlband und herstellungsverfahren
EP2430199B1 (de) Verfahren zur herstellung eines warmgewalzen stahlbandes und warmgewalztes stahlband produkt
EP2778247A1 (de) Stahlblech für heisspressformen, heisspressformelement und herstellungsverfahren dafür
EP2647730A2 (de) Verfahren zur Herstellung eines hochfesten formbaren durchlaufgeglühten Stahlstreifens, hochfestes formbares durchlaufgeglühtes Produkt und Stahlspule
JP2005126733A (ja) 高温加工性にすぐれた熱間プレス用鋼板及び自動車用部材
EP3085801B1 (de) Heissgepresstes stahlblech und verfahren zu dessen herstellung
KR101759915B1 (ko) 금속 스트립 제조 방법
EP2883974B1 (de) Walzdraht mit guter festigkeit und duktilität sowie herstellungsverfahren dafür
CN110832100B (zh) 用于拼焊板的钢材料及使用该钢材制造热冲压部件的方法
EP3186406B1 (de) Kaltgewalztes, hochfestes, niedriglegiertes stahlband
EP3327164A1 (de) Feuerverzinktes galvanisiertes stahlblech und feuerverzinktes galvannealed-stahlblech mit hervorragender altersbeständigkeitseigenschaften und brennhärtbarkeit sowie verfahren zur herstellung davon
EP0322463B1 (de) Durch wärmrbehandlung härtbares warmgewalztes stahlfeinblech mit ausgezeichneter kaltverformbarkeit und verfahren zu seiner herstellung
US20230010877A1 (en) Method of making a cold formable high strength steel strip and steel strip
CN104245970A (zh) 低屈服比高强度电阻焊钢管、用于该电阻焊钢管的钢带以及它们的制造方法
US20210301364A1 (en) Producing a hardened steel product
CN108474084B (zh) 加工性优异的热轧镀覆钢板及其制造方法
KR101736634B1 (ko) 연성과 구멍가공성이 우수한 고강도 냉연강판, 용융아연도금강판 및 이들의 제조방법
EP3822383B1 (de) Warmgewalztes beschichtetes stahlblech mit hoher festigkeit, hoher verformbarkeit, hervorragender backhärtbarkeit und verfahren zu seiner herstellung
JP4158034B2 (ja) 薄鋼板の熱間圧延方法
WO2023089950A1 (ja) 厚鋼板およびその製造方法

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 20100219

AK Designated contracting states

Kind code of ref document: A2

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MT NL NO PL PT RO SE SI SK TR

AX Request for extension of the european patent

Extension state: AL BA MK RS

DAX Request for extension of the european patent (deleted)
RAP1 Party data changed (applicant data changed or rights of an application transferred)

Owner name: TATA STEEL IJMUIDEN BV

17Q First examination report despatched

Effective date: 20121220

RAP1 Party data changed (applicant data changed or rights of an application transferred)

Owner name: MUHR UND BENDER KG

RAP1 Party data changed (applicant data changed or rights of an application transferred)

Owner name: MUHR UND BENDER KG

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: GRANT OF PATENT IS INTENDED

INTG Intention to grant announced

Effective date: 20170410

RIN1 Information on inventor provided before grant (corrected)

Inventor name: HOL, CAMILE WILBERT JOSE

Inventor name: VAN POPTA, PIETER JACOB

Inventor name: WU, HAI

Inventor name: VERLOOP, WILLEM CORNELIS

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE PATENT HAS BEEN GRANTED

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MT NL NO PL PT RO SE SI SK TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 928191

Country of ref document: AT

Kind code of ref document: T

Effective date: 20171015

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602008052097

Country of ref document: DE

REG Reference to a national code

Ref country code: SE

Ref legal event code: TRGR

REG Reference to a national code

Ref country code: NL

Ref legal event code: FP

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20171213

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170913

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170913

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170913

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20171213

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20171214

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170913

Ref country code: ES

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170913

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 11

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170913

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170913

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170913

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180113

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602008052097

Country of ref document: DE

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170913

26N No opposition filed

Effective date: 20180614

REG Reference to a national code

Ref country code: HU

Ref legal event code: AG4A

Ref document number: E037337

Country of ref document: HU

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170913

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170913

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180319

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180319

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180331

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180331

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: NL

Payment date: 20190227

Year of fee payment: 12

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: GB

Payment date: 20190321

Year of fee payment: 12

Ref country code: FR

Payment date: 20190322

Year of fee payment: 12

Ref country code: IT

Payment date: 20190225

Year of fee payment: 12

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: AT

Payment date: 20190321

Year of fee payment: 12

Ref country code: SE

Payment date: 20190318

Year of fee payment: 12

Ref country code: BE

Payment date: 20190320

Year of fee payment: 12

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180319

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170913

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170913

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170913

REG Reference to a national code

Ref country code: NL

Ref legal event code: MM

Effective date: 20200401

REG Reference to a national code

Ref country code: AT

Ref legal event code: MM01

Ref document number: 928191

Country of ref document: AT

Kind code of ref document: T

Effective date: 20200319

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20200331

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NL

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200401

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200319

Ref country code: SE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200320

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200331

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200331

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20200319

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200319

REG Reference to a national code

Ref country code: AT

Ref legal event code: UEP

Ref document number: 928191

Country of ref document: AT

Kind code of ref document: T

Effective date: 20170913

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200319

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: PL

Payment date: 20230221

Year of fee payment: 16

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: HU

Payment date: 20240216

Year of fee payment: 17

Ref country code: DE

Payment date: 20240304

Year of fee payment: 17

Ref country code: SK

Payment date: 20240223

Year of fee payment: 17